Hydrogen-absorbing alloy for battery, method of manufacturing the same, and secondary nickel-metal hydride battery

ABSTRACT

A hydrogen-absorbing alloy for battery according to the present invention comprises an alloy having the composition represented by a general formula A Ni a  Mn b  M c   where, A is at least one kind of element selected from rare earth elements including Y (yttrium), M is a metal mainly composed of at least one kind of element selected from Co, Al, Fe, Si, Cr, Cu, Ti, Zr, Zn, Hf, V, Nb, Ta, Mo, W, Ag, Pd, B, Ga, In, Ge and Sn, 3.5≦a≦5, 0.1≦b≦1, 0≦c≦1, 4.5≦a+b+c≦6!, wherein the alloy has columnar structures in which the area ratio of the columnar structures having the ratio of a minor diameter to a major diameter (aspect ratio) of 1:2 or higher is 50% or more. Further, an average minor diameter of the columnar structures is set to 30 microns or less. With this arrangement, there can be provided a nickel-metal hydride battery capable of satisfying the three leading characteristics of a high electrode capacity, long life and good rising-up all together.

This is a Division of application Ser. No. 08/452,544 filed on May 30,1995, now U.S. Pat. No. 5,654,115 which is a continuation of applicationSer. No. 08/120,412, filed on Sep. 14, 1993, abandoned.

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to a hydrogen-absorbing alloy for abattery, a method of manufacturing the same and a nickel-metal hydridebattery using the alloy, and more specifically, to a hydrogen-absorbingalloy for a battery capable of, when applied to a negative electrode ofthe battery, satisfying all of the three leading characteristics or ahigh electrode capacity (battery capacity), long life (long cycle life)durable for repeated use and excellent initial activity as well as astabilized electric potential (evenness of a voltage), a method ofmanufacturing the same and a secondary nickel-metal hydride battery.

2. Description of the Related Art

Recently, the miniaturization and portability of electronic appliances,which cannot be conventionally expected, has been achieved by theprogress of a power saving technology and mounting technology realizedby the progress of electronics. Under such a circumstance, a secondarybattery used as a power source of these electronic appliances isrequired to have a large capacity and long life. For example, in thefield of office automation appliances, telephone devices, audio/visualappliances having been developed for personal use and portable use, thedevelopment of battery having a high performance is desired to operatethese appliance for a longer time without using a power supply cable.Although a non-sintering type nickel-cadmium battery having theelectrode substrate, which is composed of three-dimensional structure,of a conventional sintering type nickel-cadmium battery has beendeveloped, the capacity of this battery has not been remarkablyincreased.

Thus, there is recently proposed and highlighted a secondary alkalinebattery (secondary nickel-metal hydride battery) using thehydrogen-absorbing alloy powder fixed to a collector as a negativeelectrode. The electrode used to this nickel-metal hydride battery ismade by the following procedure. That is, hydrogen-absorbing alloy ismelted by a high frequency induction melting method, arc melting methodor the like and then cooled and pulverized and the thus obtainedpulverized powder is added with an electric conductive agent and binderto form a kneaded material, and this kneaded material is coated to orpressingly attached to a collector. The negative electrode using thehydrogen-absorbing alloy is characterized in that it can not onlyincrease an effective energy density per a unit weight or capacity butalso has a less amount of poisonous property and a less possibility ofenvironmental pollution as compared with cadmium used as a material forthe negative electrode of a conventional typical secondary alkalinebattery.

The negative electrode containing the hydrogen-absorbing alloy, however,is immersed into a thick alkaline solution as a battery electrolyte whenit is assembled to a secondary battery as well as exposed to oxygenevolved from a positive electrode when the battery is excessivelycharged, and thus the hydrogen-absorbing alloy is corroded and theelectrode characteristics thereof are liable to be deteriorated.Further, when the battery is charged, hydrogen is absorbed into andreleased from the hydrogen-absorbing alloy to cause the volume of thealloy to be expanded and shrank, and thus cracks are produced to thehydrogen-absorbing alloy, by which the pulverization of thehydrogen-absorbing alloy is progressed. When the pulverization of thehydrogen-absorbing alloy is progressed, the increase of the specificsurface area of the hydrogen-absorbing alloy is accelerated, and thusthe ratio of the surface area of the hydrogen-absorbing alloydeteriorated by the alkaline battery electrolyte is increased.

Moreover, since the electric conductivity between the hydrogen-absorbingalloy and the collector is also deteriorated, a cycle life is shortenedas well as the electrode characteristics are also deteriorated.

To solve the above problems, although there are proposed such methods asproviding the hydrogen-absorbing alloy with a multi-element structure,preventing the direct contact of the hydrogen-absorbing alloy with thebattery electrolyte by covering a copper thin film or nickel thin filmonto the surface of the hydrogen-absorbing alloy powder or the surfaceof a negative electrode containing the hydrogen-absorbing alloy by aplating method, vapor deposition method or the like to improve thecorrosion resistance of the hydrogen-absorbing alloy, preventing cracksby increasing the mechanical strength of the hydrogen-absorbing alloy,or suppressing the deterioration of the surface of thehydrogen-absorbing alloy by drying the same after it has been immersedinto an alkaline solution, these methods cannot always achieve asufficient improvement and sometimes lower an electrode capacity on thecontrary.

Further, as described above, although the electrode characteristics ofthe conventional hydrogen-absorbing alloy are deteriorated by a kind ofcorrosive reaction caused by the alkaline battery electrolyte, thebattery electrolyte is consumed by the reaction. Therefore, the batteryelectrolyte in the conventional battery has an amount larger than thatnecessary to smoothly cause a battery reaction so that the batteryreaction is not prevented even if the amount of the battery electrolyteis reduced to some extent. When, however, the amount of the electrolyteis increased and the surface of the hydrogen-absorbing alloy electrodeis covered with it, the reaction speed for consuming an oxygen gasevolved in an excessively charged region is lowered, and thus a problemarises in that a battery internal pressure is increased.

Further, the aforesaid deterioration of the hydrogen-absorbing alloy isalso a problem when battery is designed.

That is, a secondary alkaline battery is designed to sealed in such amanner that when the battery is discharged, a portion of thehydrogen-absorbing alloy electrode usually remains in a charged stateand when the battery is charged, a portion of the hydrogen-absorbingalloy electrode partially remains in an uncharged state. Since, however,the hydrogen-absorbing alloy is deteriorated with the progress of chargeand discharge, a large amount of the hydrogen-absorbing alloy must becontained so that the above relationship can be maintained even if thealloy is deteriorated in order to obtain a sufficient cycle life as abattery. Consequently, since the volume of a nickel electrode as acapacity-limiting electrode is reduced and the volume of thehydrogen-absorbing alloy electrode is increased, the increase of thebattery capacity is prevented as well as a cost of the battery isincreased because the hydrogen-absorbing alloy is expensive.

Incidentally, the aforesaid hydrogen-absorbing alloy is composed of, forexample, AB₂ type or A₂ B type hydrogen-absorbing alloy represented byZr--Ti--Mn--Fe--Ag--V--Al--W, Ti₁₅ Zr₂₁ V₁₅ Ni₂₉ Cr₅ Co₅ Fe₁ Mn₈ and thelike. These hydrogen-absorbing alloys are made by a usual method ofpulverizing an alloy made by being melted and cast. When this series ofalloys are used to a negative electrode, they exhibit a high electrodecapacity and provide a good capacity of about 300 mAh/g, 400 mAh/g,respectively as well as almost all the metal materials constituting thealloys are less expensive.

These alloys, however, have a drawback in that they are generallydifficult to be made to have a composition distributed uniformly.Further, a battery using this series of alloys as an electrode materialhas a drawback in that the battery has a delayed rising-up of acapacity, and thus a high electrode capacity can be obtained for thefirst time after an activating operation (charge/discharge operation) ofseveral tens of cycles is repeated after the battery has been assembled.Moreover, this series of alloys also have a drawback in that dischargingcharacteristics are bad in a large current and further a voltage greatlydrops at a low temperature. That is, this series of the alloys cannotachieve the high capacity in the three leading characteristics or a highelectrode capacity, long life and excellent initial activity, whereasthey cannot satisfy the technical requirements in the aspect of theinitial activity (rising-up property).

On the other hand, there is an AB₅ type alloy represented by LaNi₅ asanother hydrogen-absorbing alloy used to secondary alkaline battery. Anegative electrode using this series of an alloy having ahexagonal-crystal structure has the feature that it can increase theeffective energy density per a unit weight or unit volume of a batteryand a battery capacity as well as has a less possibility to cause theenvironmental pollution due to cadmium and the like and good batterycharacteristics when compared with the case in which cadmium as aconventional typical negative electrode material for secondary alkalinebattery is used. Further, the battery using the AB₅ type alloy has anadvantage that it can discharge a large current. In this connection, anAB₅ type hydrogen-absorbing alloy composed of Mm--Ni--Co--Al alloy (Mmis referred to as misch metal) has a low electrode capacity of less than200 mAh/g and a cycle life determined by charge/discharge is about 400cycles, which does not reach the level for satisfying the electrodecapacity and cycle life needed by the recent technical requirements.

Thus, a technology of relatively increasing the content ratio of the Asite is also employed to increase the electrode capacity of the batteryusing the AB₅ type hydrogen-absorbing alloy. According to thistechnology, although the electrode capacity can be increased by about30%, a drawback arises in that the charge/discharge cycle life isshortened.

Further, there is also employed a technology for increasing the amountof La content in misch metal (Mm: a mixture of rare earth elementscontaining 10-50 wt % of La, 5-60 wt % of Ce, 2-10 wt % of Pr, 10-45 wt% of Nd and the like) constituting the A component. That is, it ispossible to increase the electrode capacity by about 30% by using mischmetal containing an reduced amount of a Ce element and a relativelyincreased amount of La. In this case, however, it is also difficult toincrease the cycle life.

As described above, a hydrogen-absorbing alloy suitable for secondarynickel-metal hydride battery for satisfying the electrode capacity,cycle life, initial rising-up characteristics and stability of electricpotential required by the recent technical level is not yet realized forpractical use.

SUMMARY OF THE INVENTION

A first object of the present invention made to solve the above problemsis to provide a hydrogen-absorbing alloy for battery capable ofsatisfying three leading characteristics of a high electrode capacity,long life and good rising-up together, a method of manufacturing thesame and a secondary nickel-metal hydride battery using thehydrogen-absorbing alloy.

A second object of the present invention is to provide ahydrogen-absorbing alloy for battery particularly excellent in long lifecharacteristics when used as a negative electrode activating material ofa secondary nickel-metal hydride battery and a secondary nickel-metalhydride battery using the hydrogen-absorbing alloy.

A third object of the present invention is to provide a secondarynickel-metal hydride battery having a high capacity and long life andfurther made by low cost by using a hydrogen-absorbing alloy having aless amount of deterioration and limiting the amount of a batteryelectrolyte and an electrode capacity ratio.

To achieve the first object, the inventors selected an AB₅ typehydrogen-absorbing alloy as an object to be studied, taking intoconsideration the point that an electrode capacity can be easilyincreased and the point that hydrogen can be absorbed/released in thevicinity of an ordinary temperature and ordinary pressure. Then, theinventors trially made hydrogen-absorbing alloys having variouscompositions by substituting the components of the AB₅ type alloy forvarious elements and changing manufacturing methods and studied theeffect of the compositions, manufacturing methods, heat treatmentconditions and the like of the hydrogen-absorbing alloys on batterycharacteristics. As a result, a knowledge as described below wasobtained step by step.

First, an invention for achieving the first object will be described. Itis found that when a part of the AB₅ type hydrogen-absorbing alloy issubstituted for Mn, an electrode capacity can be greatly improved toabout 280 mAh/g. The inventors find, however, the fact that when asubstituted amount of Mn exceeds a predetermined amount, the corrosionresistance of the hydrogen-absorbing alloy is lowered and the lifecharacteristics of a battery using the hydrogen-absorbing alloy arelowered on the contrary.

More specifically, a problem is made clear that the corrosion caused bya thick alkaline solution as the battery electrolyte of a secondaryalkaline battery is liable to progress particularly when the solutioncoexists with oxygen produced when the battery is excessively charged,and thus the battery characteristics are deteriorated.

Then, the inventors studied the reason why the life characteristics ofthe battery is lowered by the addition of Mn. When the elementsconstituting various AB₅ type alloy structures added with Mn wereanalyzed by an X-ray microanalyzer, there was confirmed the tendencythat an amount of segregated Mn was increased in each alloy structurewith the increase in the substituted amount of Mn. When assumed fromthis tendency, it was found that the reduced life of battery progressedwith the increase in the substituted amount of Mn was mainly caused bythe segregations of Mn.

That is, when a casting method having a low cooling capability as aconventional method of manufacturing hydrogen-absorbing alloy is used,since crystals are grown isotropic in a cooling process, particleboundaries are liable to be made irregular in the particles of ahydrogen-absorbing alloy as well as the alloy exists in a liquid phasestate for a long time, and thus segregations are liable to be made toparticle boundaries. Further, even if columnar crystals are partiallyformed by using a casting method having a high cooling capability, thecrystal growth with columnar structure in a minor diameter direction isprogressed, segregation is promoted and the corrosion resistance of analloy is liable to be lowered. Further, Mn has a feature that it is moreembrittle than other alloy-constituting elements. As a result, thesegregations on the particle boundaries act as a starting point ofcorrosion as well as a mechanical strength is lowered by thesegregations, and thus the alloy is remarkably pulverized.

Further, it is supposed that the segregations in the hydrogen-absorbingalloy are liable to form a local battery, Mn is solved out into analkaline battery electrolyte by the electric erosive action thereof andMn on the surface of the alloy is changed to Mn(OH)₂ to therebyaccelerate the corrosion of the alloy, and thus the amount of hydrogenabsorbed to the hydrogen-absorbing alloy itself is reduced and a batterycapacity is lowered by electrode exfoliated from the hydrogen-absorbingalloy by being corroded. Further, it is also supposed that thepulverization of the alloy is accelerated by the reduced strength of theparticle boundaries caused by the segregation, and thus thedeterioration of battery characteristics is progressed with age.

From the facts mentioned above, it can be expected to obtain ahydrogen-absorbing alloy having a high capacity and long life byreducing the segregations of Mn.

Thus, the following methods were executed by the inventors as a trial toreduce the segregations of Mn:

(1) when an alloy material was melted, it was put into a crucible afterit had been pulverized as much as possible and sufficiently mixed. Thealloy material was relatively well mixed in a molten state, however,segregations were formed in the size of from several tens of microns toseveral hundreds of microns when cooled;

(2) when the alloy material was melted, a resistance heating member wasnot used but a high frequency induction heating apparatus was used andthe molten alloy was forcibly stirred, and in this case, although thealloy was very uniformly stirred in a molten state, segregations wereformed in the size of from several tens of microns to several hundredsof microns when cooled;

(3) when a molten alloy was cast, it was homogenized by lowering theviscosity of the molten alloy by increasing the temperature thereof ashigh as possible and in this case, however, segregations were formed inthe size of from several tens of microns to several hundreds of micronswhen cooled; and

(4) after the molten alloy had been cast, it was subjected to a heattreatment (e.g., at 1000° C. for 8 hours) to reduce the segregations,and in this case, although the effect of the heat treatment was large,segregations of the size of several tens of microns remained.

As described above, even if a processing was executed by any one of themethods or by combining two or more of the methods, requiredcharacteristics could not be sufficiently satisfied althoughsegregations were reduced.

As a result of the various studies of countermeasures for preventing thesegregations of Mn and the like effected by the inventors, at first, theinventors employed a method of quenching an molten alloy having apredetermined composition containing Mn at a quenching rate of1000°-1200° C./sec. which was higher than that of a conventional castingmethod.

Although this method could reduce the segregations of Mn, it also couldnot satisfy the required characteristics.

Thus, the experiment was further continued by employing a high quenchingrate of 1800° C./sec. or more. As a result, it was discovered that theresult of the experiment was completely different from that obtainedfrom the low quenching rate in the range of 1000°-1200° C./sec. Morespecifically, it was discovered that when the quenching rate was 1800°C./sec. or higher, the maximum value of the Mn concentration distributedin the alloy was 1.3 times or less the average value of the Mnconcentration in the entire alloy as well as the maximum diameter of Mnsegregated in the alloy was 0.5 micron or less.

Further, it was found that when the alloy having the above Mndistribution was applied to secondary nickel-metal hydride battery, thecharge/discharge cycle life characteristics of the battery was greatlyimproved without lowering capacity characteristics.

Here, first, the distribution of the Mn concentration will be described.In the hydrogen-absorbing alloy in which the maximum value of the Mnconcentration distributed in the alloy exhibits a value exceeding 1.3times the average value of the Mn concentration in the entire alloy,locations having a partially large Mn concentration are scattered in thealloy.

When the alloy is used to the negative electrode of nickel-metal hydridebattery, a corrosive reaction is liable to be caused in these locationsand the deterioration of the hydrogen-absorbing alloy itself is liableto be progressed. Further, when the locations having the different Mnconcentration exist as described above, the degree ofexpansion/shrinkage of the volume of the hydrogen-absorbing alloy causedby the hydrogen absorption/release due to a battery reaction ispartially different, and thus the pulverization of the alloy is liableto be progressed by the stress caused in the alloy. Therefore, thedeterioration of the hydrogen-absorbing alloy is further progressed bythe increase in the specific surface area resulting from thepulverization.

The above phenomenon is difficult to be caused in the hydrogen-absorbingalloy in which the maximum value of the Mn concentration distributed inthe alloy exhibits a value 1.3 times or less the average value of the Mnconcentration in the entire alloy. Consequently, it is supposed thatwhen this alloy is applied to a negative electrode, the progress ofcorrosion of the alloy can be suppressed and the cycle lifecharacteristics of the nickel-metal hydride battery is improved.

FIG. 29 shows the relationship between the ratio of the maximum value ofthe Mn concentration in the alloy to the average value of the Mnconcentration in the entire alloy and the cycle life of the batteryobtained from the experiment of the inventors.

The graph of FIG. 29 shows that a peculiar point exists in the vicinityof the point where the maximum value of the Mn concentration is 1.3times the average value thereof. That is, the inventors have discoveredfor the first time the fact that battery life characteristics aregreatly changed on the boundary of the peculiar point where the maximumvalue of the Mn concentration reaches 1.3 time the average valuethereof.

Next, the maximum diameter of segregated Mn will be described. Since thehydrogen-absorbing alloy in which the segregated Mn has a maximumdiameter of 0.5 micron has a large segregated portion, when this alloyis used to a nickel-metal hydride battery, the segregated point acts asthe starting point of a corrosive reaction and the deterioration of thealloy itself is liable to be progressed. Further, when the alloy isexpanded/shrank by the hydrogen absorption/release caused by a batteryreaction, since stress is concentrated to the Mn segregated point,cracks are liable to be caused from the segregated point andpulverization is further progressed.

On the other hand, the above phenomenon is difficult to be caused in thehydrogen-absorbing alloy in which the segregated Mn has a maximumdiameter 0.5 micron or less.

Therefore, it is supposed that when this alloy is applied to thenegative electrode of a nickel-metal hydride battery, the progress ofcorrosion of the negative electrode is suppressed and thus the cyclelife characteristics of the nickel-metal hydride battery is improved.

FIG. 30 shows the result of measurement of the maximum Mn diametersegregated in the alloy and the cycle life of the electrode using thisalloy obtained by an experiment.

It is found from the graph shown in FIG. 30 that a peculiar point existsin the vicinity of the location where the maximum value of Mn segregatedin the alloy is 0.5 micron. That is, the inventors have discovered forthe first time the fact that a battery life is greatly changed on theboundary of the peculiar point where the maximum diameter of segregatedMn is 0.5 micron.

As described above, the inventors have found for the first time that thepeculiar points exist between the distribution of the Mn concentrationand the maximum diameter of segregated Mn and the requiredcharacteristics of battery and that hydrogen-absorbing alloy must beprepared by quenching a molten alloy at a quenching rate of 1800°C./sec. or higher to achieve the uniformity of the Mn concentration andthe reduction of segregations, and thus the above object cannot beachieved by the conventional low quenching rate of about 1000°-1200°C./sec.

Further, a columnar crystal structure with a special or novel shapecould be made for the first time by the high quenching rate of 1800°C./sec. or higher (refer to Table 11).

The columnar crystal structure with the novel shape is composed ofcrystal particles in which the ratio of minor diameter to major diameter(aspect ratio) of columnar crystal particles is 1:2 or higher. Then, ithas been discovered that when the ratio of fine columnar crystalsoccupying in the cross section of the pulverized particles of the alloyis 50% or higher, preferably 70% or higher and more preferably 80% orhigher, a higher electrode capacity and longer life cycle can beachieved at the same time. That is, it has been discovered for the firsttime that when the above fine columnar crystal structure is formed, thehigh electrode capacity of 240 mAh/g or more and long cycle life of 500times or more are achieved at the same time.

That is, as a result of the various studies effected by the inventors,it has been discovered that the characteristics of thehydrogen-absorbing alloy as a negative electrode material can be greatlyimproved by forming fine crystal particles having a predeterminedfeature in the alloy by a rapidly-quenched method from the melt at aquenching rate of 1800° C./sec. or higher.

As a result of the examination effected by the inventors, thehydrogen-absorbing alloy made by the rapidly-quenched method from themelt can effectively prevent the segregations of Mn and the like.

Further, the inventors have obtained the knowledge that ahydrogen-absorbing alloy for battery more excellent in characteristicscan be obtained by removing the fine internal distortion produced by arapid quenching process, by taking attention to the internal distortion.More specifically, when an alloy material in a molten state is rapidlyquenched by the above method, the quenching is rapidly executed byforming many crystal nuclei, different from a casting method, and thusdistortion is liable to be made in the interior of the alloy by thequenching. It is found that hydrogen is difficult to enter into theinterior of such alloy and to exit therefrom due to the formation of theinternal distortion, by which battery characteristics are degraded.

Thus, as a result of various studies, the inventors have obtained theknowledge that in the case of the hydrogen-absorbing alloy according tothe present invention having formed once the fine crystal structure bythe rapidly-quenched method from the melt, the internal distortion canbe removed while keeping the uniformity of the alloy by only subjectingthe alloy to a heat treatment within the temperature range of 200°-500°C. which is far lower than a recrystallizing temperature for a shorttime, thus a hydrogen-absorbing alloy for battery more excellent in thecharacteristics can be obtained.

More specifically, it has been found that the mitigation of the internaldistortion by the heat treatment enables hydrogen to more easily enterinto and exit from the interior of the alloy so that the characteristicsof a negative electrode material can be further improved. At least onehour is necessary for the heat treatment.

The present invention has been completed based on the above variousknowledges and findings. That is, a first hydrogen-absorbing alloyaccording to the present invention comprises an alloy having thecomposition represented by a general formula A Ni_(a) Mn_(b) M_(c)where, A is at least one kind of element selected from rare earthelements including Y (yttrium), M is a metal mainly composed of at leastone kind of element selected from Co, Al, Fe, Si, Cr, Cu, Ti, Zr, Zn,Hf, V, Nb, Ta, Mo, W, Ag, Pd, B, Ga, In, Ge and Sn, 3.5≦a≦5, 0.1≦b≦1,0≦c≦1, 4.5≦a+b+c≦6!, wherein the alloy has a columnar structure in whichthe area ratio of columnar structure having the ratio of a minordiameter to a major diameter (aspect ratio) of 1:2 or higher is 50% ormore. More specifically, an electrode capacity is increased bysubstituting a portion of the B component of an AB₅ typehydrogen-absorbing alloy for Mn as well as a hydrogen-absorbing alloywith a novel shape capable of forming an electrode having a long cyclelife is formed.

Further, when the above alloy is made by the rapidly quenching process,the rapidly-quenched molten alloy preferably has a thickness set to10-150 microns. In addition, the columnar crystals preferably have anaverage minor diameter of 30 microns or less.

A second hydrogen-absorbing alloy according to the present inventioncomprises an alloy having the composition represented by a generalformula A Ni_(a) Mn_(b) M_(c) where, A is at least one kind of elementselected from rare earth elements including Y (yttrium), M is a metalmainly composed of at least one kind of element selected from Co, Al,Fe, Si, Cr, Cu, Ti, Zr, Zn, Hf, V, Nb, Ta, Mo, W, Ag, Pd, B, Ga, In, Geand Sn, 3.5≦a≦5, 0.1≦b≦1, 0≦c≦1, 4.5≦a+b+c≦6!, wherein when thecharacteristic X-ray intensity of Mn contained in the alloy is observedby an X-ray microanalyzer in the respective unit regions of the alloyobtained by vertically and horizontally dividing into 100 portions theobservation regions of the alloy each composed of a cross sectional areaof 20 microns×20 microns, the maximum value among the characteristicX-ray intensities of Mn in the respective observation regions is 1.3times or less the average value of the characteristic X-ray intensitiesof Mn in the respective observation regions. The aforesaid value of (themaximum value of the Mn concentration in the alloy)/(the average valueof the Mn concentration in the alloy) can approximate (the maximum valueamong the characteristic X-ray intensities of Mn in the respective unitregions)/(the average value of the characteristic X-ray intensities ofMn in the respective unit regions) when observed by the X-raymicroanalyzer in the respective unit regions of the alloy obtained byvertically and horizontally dividing into 100 portions the observationregions of the alloy each composed of a cross sectional area of 20microns×20 microns. In the present invention, this value is set to 1.3or less, and more preferably set to 1.2 or less.

Further, a third hydrogen-absorbing alloy according to the presentinvention comprises an alloy having the composition represented by ageneral formula A Ni_(a) Mn_(b) M_(c) where, A is at least one kind ofelement selected from rare earth elements including Y (yttrium), M is ametal mainly composed of at least one kind of element selected from Co,Al, Fe, Si, Cr, Cu, Ti, Zr, Zn, Hf, V, Nb, Ta, Mo, W, Ag, Pd, B, Ga, In,Ge and Sn, 3.5≦a≦5, 0.1≦b≦1, 0≦c≦1, 4.5≦a+b+c≦6!, wherein the maximumdiameter of the Mn particles segregated in the alloy is 0.5 micron orless.

A first manufacturing method of a hydrogen-absorbing alloy for batteryaccording to the present invention comprises the step of injecting amolten alloy having the composition represented by a general formula ANi_(a) Mn_(b) M_(c) where, A is at least one kind of element selectedfrom rare earth elements including Y (yttrium), M is a metal mainlycomposed of at least one kind of element selected from Co, Al, Fe, Si,Cr, Cu, Ti, Zr, Zn, Hf, V, Nb, Ta, Mo, W, Ag, Pd, B, Ga, In, Ge and Sn,3.5≦a≦5, 0.1≦b≦1, 0≦c≦1, 4.5≦a+b+c≦6! onto the traveling surface of acooling roll(s) rotating at a high speed and rapidly quenching andsolidifying the molten alloy at a quenching rate of 1800° C./sec. orhigher to form the hydrogen-absorbing alloy.

A second manufacturing method of a hydrogen-absorbing alloy for batteryaccording to the present invention comprises the steps of rapidlyquenching a molten metal having the aforesaid composition at a quenchingrate of 1800° C./sec. or higher and subjecting the thus obtainedrapidly-quenched molten alloy to a heat treatment at the temperaturerange of from 200°-500° C. for at least one hour to form ahydrogen-absorbing alloy for battery.

Further, the rapid quenching process of the molten alloy is preferablyexecuted in vacuum or an atmosphere of an inert gas such as Ar. Inaddition, the heat treatment is preferably executed in vacuum or aninert gas atmosphere.

In the first to third hydrogen-absorbing alloys for battery according tothe present invention, when Ni_(a) Mn_(b) M_(c) are represented by B,the alloy composition according to the present invention is AB₄.6 -AB₆from 4.5≦a+b+c≦6.

When the composition ratio x of B (i.e., the value of a+b+c) is otherthan the above range, the amount of phases (for example, phases composedof AB, AB₂, AB₃, A₂ B₇ and the like and a phase composed of a singleelement constituting a B site, hereinafter, referred to as a secondphase!) other than AB₄.5 -AB₆ created in the alloy is increased.

When the amount of the second phase other than AB_(x) is increased inthe alloy, the ratio of the alloy phases which have two or moredifferent compositions including the second phase and come into contactwith one another is increased in the hydrogen-absorbing alloy. Theboundaries of the alloy phases having the different compositions areweak in a mechanical strength and cracks are liable to be made fromthese boundaries by the absorption/release of hydrogen.

Further, segregations are liable to be made to the boundaries and thehydrogen-absorbing alloy is liable to be corroded from the segregations.Further, the second phase absorbs a less amount of hydrogen as comparedwith AB_(x) when used as an electrode, and thus when an alloy includinga large amount of the second phase as the electrode, an electrodecapacity per a unit volume is reduced. In any way, when thehydrogen-absorbing alloy is used as an electrode material, it reducesthe electrode capacity and life.

After all, the reason why the value of x is limited is as follows. Whenx is less than 4.5, a hydrogen-absorbing alloy which is less corrodedwhen a battery is charged/discharged and difficult to be cracked andpulverized cannot be obtained. On the other hand, when x exceeds 6, thecreation of the second phase is admitted in an alloy making method whichcan be usually employed in the industry and thus the characteristics ofthe hydrogen-absorbing alloy cannot be improved.

Therefore, although the value of x or (a+b+c) is set within the range of4.5-6, it is preferably 4.6-5.6 and more preferably within the range of5.05-5.5.

The component A constituting A Ni_(a) Mn_(b) M_(c) according to thepresent invention shows at least one kind selected from rare earthelements including Y (specifically, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd,Tb, Dy, Ho, Er, Tm, Yb, Lu). Note, since rare earth elements of highpurity or a rare earth element as a single element are very expensive.Thus, the material cost of the hydrogen-absorbing alloy can be greatlyreduced by using a misch metal (hereinafter, abbreviated as Mm or Lm) asa mixture of a plurality of rare earth elements. A compositioncontaining La of 10-50 wt %, Ce of 5-60 wt %, Pr of 2-10 wt %, Nd of10-45 wt % is usually used as the Mm.

Further, the reason why the value of the composition ratio a of Ni islimited within the range of 3.5-5 is as follows. When the value a is setto less than 3.5, the electrode capacity is lowered, whereas when thevalue a exceeds 5, the mixing ratio of other alloy components isrelatively lowered and thus the capacity is difficult to be increased.

Further, since Mn is effective to increase the capacity of the negativeelectrode containing the hydrogen-absorbing alloy and reduce a hydrogenabsorption/release pressure (equilibrium pressure), it is used as anessential element constituting the alloy of the present invention. Mn isadded within such a range that the constitution ratio b thereof is0.1-1.0. When the constitution ratio b exceeds 1, the alloy electrode isliable to be pulverized and its cycle life is shortened, and thus theupper limit of the constitution ratio b is set to 1. On the other hand,when the constitution ratio b of Mn is less than 0.1, the improvement ofthe electrode capacity as one of the objects of the present inventioncannot be achieved.

Further, the component M in a general formula shows a metal mainlycomposed of at least one kind of element selected from Co, Al, Fe, Si,Cr, Cu, Ti, Zr, Zn, Hf, V, Nb, Ta, Mo, W, Ag, Pd, B, Ga, In, Ge and Sn.The elements Co, Al, Fe, Si, Cr, Cu of the component M are particularlyeffective to extend the life of the hydrogen-absorbing alloy. The Mcomponent is added within such a range that the constitution ratio cthereof is 1 or less. When the constitution ratio c exceeds 1, thecapacity of the electrode formed of the alloy lowered, and thus theupper limit of the constitution ratio c is set to 1.

Further, when the alloy is made by using a rapidly-quenched method fromthe melt, a life can be extended to some extent because segregations areprevented. Therefore, the lower limit of the composition ratio c of thecomponent M is set to 0.

Al of the component M has a function for lowering the hydrogenabsorbing/releasing pressure (dissociation) in the same way as Mn aswell as can increase durability.

Further, Co of the component M is effective to improve the corrosionresistance of the alloy against a battery electrolyte and the like andthe pulverization of the alloy is greatly suppressed by it. Morespecifically, when the substituted amount of Co is increased, the cyclelife is increased but there is the tendency that the electrode capacityand the high rate discharge ability are lowered, and thus thesubstituted amount of Co must be optimized in accordance with theapplication of battery.

In addition to the above, the hydrogen-absorbing alloy according to thepresent invention may contain at least one kind of element selected fromPb, C, N, O, F Cl, S, P and the like as impurities in the range by whichthe characteristics of the alloy of the present invention is notobstructed.

The content of the impurities is preferably in the range of 6000 ppm orless, more preferably 5000 ppm or less and still more preferably 4000ppm.

Although a method of manufacturing the hydrogen-absorbing alloy forbattery according to the present invention is not particularly limitedso long as it can make a uniform alloy composition, prevent segregationsand obtain the crystal structure according to the present invention, thehydrogen-absorbing alloy can be stably manufactured in a large amount byusing a molten-metal-rapidly-quenching method such as a single rollmethod, double roll method and the like to be describe below in detailwith reference to drawings and optimizing the material of a coolingroll(s), rotating speed of the cooling roll(s) (peripheral speed of thetraveling surface thereof), a molten alloy temperature, kind of gas in acooling chamber, pressure, amount of the molten alloy to be injected.

Single Roll Method

FIG. 1 shows a hydrogen-absorbing alloy manufacturing apparatus usingthe single roll method. This manufacturing apparatus comprises a coolingroll 5 composed of copper, nickel or the like excellent in thermalconductivity and having a diameter of about 300 mm and a molten metalinjection nozzle 4 for injecting a molten hydrogen-absorbing alloy 3supplied from a ladle 2 to the traveling surface of the cooling roll 5after storing the same. The cooling roll 5 and the like are accommodatedin a cooling chamber 1 adjusted to vacuum or an inert gas atmosphere.Further, although the rotating speed of the cooling roll 5 depends uponthe wetting property thereof, cooling speed and an injection amount ofthe molten hydrogen-absorbing alloy, it is generally set to 300-5000rpm.

In the aforesaid manufacturing apparatus shown in FIG. 1, when themolten hydrogen-absorbing alloy 3 supplied from the ladle 2 is injectedonto the traveling surface of the cooling roll 5 through the moltenmetal injection nozzle 4, the molten alloy is solidified from thesurface thereof in contact with the cooling roll 5, crystals begin to begrown and the solidification of the molten metal is perfectly completedbefore it leaves from the cooling roll 5. Thereafter, the molten metalis further cooled while it flies in the cooling chamber 1 so that ahydrogen-absorbing alloy 6 is made which has the uniform concentrationof constituting elements, a less amount of segregations and crystalsgrown in the same direction.

Double Roll Method

FIG. 2 shows a hydrogen-absorbing alloy manufacturing apparatus usingthe double roll method. This manufacturing apparatus comprises a pair ormore of cooling rolls 5a, 5b disposed in a cooling chamber 1 so that therespective traveling surfaces thereof are confronted to each other, amelting furnace 7 for preparing a molten hydrogen-absorbing alloy 3 bymelting material metals, and a molten metal injection nozzle 4 forinjecting the molten hydrogen-absorbing alloy 3 supplied from themelting furnace 7 between the cooling rolls 5a, 5b through a tundish 8.

The cooling rolls 5a, 5b are composed of a material excellent in thermalconductivity such as copper, nickel or the like and having a diameter ofabout 50 mm. These cooling rolls 5a, 5b are rotated at a high speed ofabout 300-2000 rpm while keeping a fine gap d of about 0-0.5 mmtherebetween.

Note, although traveling surfaces of the cooling rolls are parallel toeach other as shown in FIG. 2, a so-called shape roll in which the crosssection of the traveling surface thereof is formed to a U-shape orV-shape may be employed. Further, when the gap d between the coolingrolls 5a, 5b is excessively large, since the molten alloy is notquenched in the same direction and as a result a hydrogen-absorbingalloy having a columnar structure whose growing direction is disturbedis made, the gap d is preferably set to 0.2 mm or less. Further, whenthe gap d is excessively large, since a quenching rate is lowered andthe segregations of Mn are accelerated, the uniformity of the Mnconcentration is lowered and a hydrogen-absorbing alloy havingsegregated particles of Mn grown to a large size on particle boundariesis made, and thus the gap d is set to 0.2 mm or less.

In the aforesaid manufacturing apparatus shown in FIG. 2, when themolten hydrogen-absorbing alloy 3 is injected in the direction betweenthe cooling rolls 5a, 5b from the injection nozzle 4, it is solidifiedfrom the sides thereof in contact with the cooling roll 5a, 5b on theboth sides, crystals begin to be grown and the solidification of themolten metal is perfectly completed before it leaves from the coolingrolls 5a, 5b. Thereafter, the molten metal is further quenched while itflies in the cooling chamber 1 so that a hydrogen-absorbing alloy 6 ismade which has a less amount of segregations and a columnar structureaccording to the present invention.

Rotating Disc Method

FIG. 32 shows a hydrogen-absorbing alloy particles manufacturingapparatus using a rotating disc method. This manufacturing apparatuscomprises a rotary disc member 9 as a high speed rotary member disposedin a cooling chamber 1 in an argon gas atmosphere and a molten metalinjection nozzle 4 for temporarily storing a molten hydrogen-absorbingalloy supplied from a ladle 2 and further injecting the same onto thetraveling surface of the rotary disc member 9. The rotary member 9 iscomposed of a ceramics or metal material having a relatively low wettingproperty to a molten metal to prevent the molten hydrogen-absorbingalloy 3 from adhering to and solidifying on the rotary member 9.

In the manufacturing apparatus shown in FIG. 32, when the moltenhydrogen-absorbing alloy 3 supplied from the ladle 2 is injected ontothe traveling surface of the rotary disc member 9 from the molten metalinjection nozzle 4, it is finely dispersed by the moving force of therotary member 9 and spheroidized by the surface tension of itself whilefrying in the cooling chamber 1 without coming into contact with theinner surface of the cooling chamber 1 and further solidified by beingquenched by the atmosphere gas such as the argon gas or the like. As aresult, hydrogen-absorbing alloy particles 6 each having a sphericalshape covered with a free cooling surface are made. Thehydrogen-absorbing alloy particles 6 are collected into a particlecollection vessel 10 disposed on the bottom of the cooling chamber 1.

Gas Atomizing Method

FIG. 33 shows a hydrogen-absorbing alloy particle manufacturingapparatus using a gas atomizing method. This manufacturing apparatuscomprises a melting furnace 24 for heating and melting a metal materialdisposed in a cooling chamber 1 in an argon gas atmosphere by a heater23 and preparing a molten hydrogen-absorbing alloy 3, a molten metalinjection nozzle 4 formed on the bottom of the melting furnace 24 andhaving an inner diameter of about 2 mm, a plurality of inert gas nozzles25 disposed in the vicinity of the lower end opening of the molten metalinjection nozzle 4 in confrontation therewith to inject an cooling inertgas such as an argon gas or the like, and a shut-off valve 26 foropening/closing the molten metal injection nozzle 4.

In the manufacturing apparatus shown in FIG. 33, when the argon gas issupplied to the melting furnace 24 in which the moltenhydrogen-absorbing alloy 3 is accommodated, the liquid surface of themolten alloy 3 in the melting furnace 24 is pressurized and the moltenalloy 3 is injected from the front end opening of the molten metalnozzle 4 on the bottom of the melting furnace 24. At this time, theinert gas nozzles 25, which are disposed substantially perpendicularlyto the direction in which the molten alloy 3 is injected, inject theinert gas such as the argon gas or the like toward the injected moltenalloy at a high speed. With this operation, the moltenhydrogen-absorbing alloy 3 is atomized and dispersed by the inert gas inthe cooling chamber 1 without coming into contact with the inner wallthereof and quenched and solidified while being flown downwardly alongthe revolution flow of the inert gas. As a result, hydrogen-absorbingalloy particles 6 each having a spherical shape covered with a freecooling surface are made.

When a ribbon-shaped, flake-shaped or particle-shaped hydrogen-absorbingalloy is made by using the aforesaid molten-metal-rapidly-quenchingmethod, equi-axed crystals and columnar structure are made in an alloystructure depending upon the conditions of the material of the coolingroll and rotary disk, quenching rate of the molten alloy and the like.

The first to third hydrogen-absorbing alloys of the present inventionare suitably obtained by rapidly quenching molten alloy particularly ata quenching rate of 1800° C./sec. or higher. Further, when thehydrogen-absorbing alloy is made by rapidly quenching the molten alloyat the quenching rate of 180° C./sec. or higher, the respective crystalparticles constituting the alloy are finely crystallized to about 1-100microns so that the strength of the alloy is increased and thedisturbance of particle boundaries is reduced, and thus an amount ofhydrogen to be absorbed is increased and the electrode capacity can beincreased.

The above columnar structure is particularly developed in the firsthydrogen-absorbing alloy for battery according to the present invention.

It has been confirmed by the experiment effected by the inventors thatsince the columnar structure has crystals grown in the same directiondifferent from those in the equi-axed crystal structure, grainboundaries are less disturbed, an amount of hydrogen to be absorbed isincreased and the electrode capacity can be increased. Morespecifically, in the columnar structure, since the paths of hydrogenmolecules or hydrogen atoms are formed along the boundaries of thecolumnar structure, hydrogen can be easily absorbed to and released fromthe alloy to thereby increase the electrode capacity. Further,segregations are greatly reduced in the columnar structure. Therefore, alocal battery is not formed by the segregations and the reduction oflife due to the pulverization of the alloy can be effectively prevented.

In the crystal structure of the hydrogen-absorbing alloy made by therapidly-quenched method from the melt, the area ratio of the columnarstructure must be 50% or more, preferably 70% or more and morepreferably 80% or more in the cross section in the thickness directionof the hydrogen-absorbing alloy, from the view point of increasingbattery characteristics when the alloy is assembled to a battery as ahydrogen-absorbing alloy electrode. When the area ratio of columnarstructure is 50% or more, the cycle life of a negative electrode usingthe alloy is extended than that of a negative electrode using ahydrogen-absorbing alloy made by a casting method. When therapidly-quenched molten alloy is entirely formed of columnar structure,segregations are particularly reduced so that the capacity and life ofan alloy electrode can be further improved. On the other hand, when thearea ratio is less than 50%, there is no remarkable difference betweenthe cycle life of the negative electrode using the above alloy and thatof the negative electrode using the alloy made by the casting method.That is, the excellent battery characteristics that the electrodecapacity is 240 mAh/g or more and the cycle life is 500 times or morecan be simultaneously obtained by using the hydrogen-absorbing alloy ofthe present invention made by the above molten-metal-rapidly-quenchingmethod and having the area ratio of the columnar structure of 50% ormore in the cross section in the thickness direction of the alloy. Themore preferable value of the electrode capacity is 250 mAh/g or more andthe still more preferable value thereof is 255 mAh/g. Further, the morepreferable value of the cycle life is 550 times or more and the stillmore preferable value thereof is 600 times or more.

Here, the columnar structure is defined as columnar crystal particleshaving a ratio of minor diameter to major diameter (aspect ratio) of 1:2or higher.

The method of manufacturing the hydrogen-absorbing alloy according tothe present invention will be described in more detail.

The hydrogen-absorbing alloy for battery having the developed columnarstructure and a reduced amount of the segregations of Mn and the like asdescribed above is made by strictly controlling the conditions forpreparing and quenching a molten alloy in the single roll method ordouble roll method or the like.

More specifically, although the molten alloy may be prepared byaccommodating a hydrogen-absorbing alloy (mother alloy) having the abovecomposition previously made by the casting method in a melting crucibleand melting the same by high frequency induction heating, it is alsopossible that respective constituting elements are directly put into acrucible after the substituted amounts thereof have been adjusted toprepare the molten alloy without using the mother alloy. At this time,it is preferable to add some elements such as, for example, rare earthelements and Mn having a high vapor pressure in a slightly greateramount in the elements constituting the hydrogen-absorbing alloy. Thatis, an adjustment is preferably made so that the change of the alloycomposition caused by the volatilization of the elements having the highvapor pressure is prevented and the hydrogen-absorbing alloy having beenrapidly quenched has a target composition.

The thus obtained molten alloy is injected onto the traveling surface(cooling surface) of the cooling roll(s) at a predetermined pressure andrapidly quenched and solidified to be made to the ribbon-shaped orflake-shaped hydrogen-absorbing alloy. At this time, columnar structureare grown from the surface of the cooling roll(s) toward the hightemperature portion of the molten alloy, that is, in the verticaldirection with respect the surface of the cooling roll(s). To enable thecolumnar structure to be sufficiently grown, the thickness of theribbon-shaped or flake-shaped hydrogen-absorbing alloy is set to therange of 10-150 microns and preferably to the range of 15-100 micronsand the peripheral speed of the traveling surface of the cooling roll(s)is set to the range of 5-15 m/sec. in the case of a copper roll and tothe range of 8-30 m/sec. in the case of an iron roll. When theperipheral speed of the cooling roll(s) is less than the lower limit ofthe above range, the molten alloy is quenched at a low quenching rateand a columnar structure cannot be sufficiently developed in the rangeof the above thickness. On the other hand, when the peripheral speed ofthe cooling roll(s) exceeds the upper limit of the above range, themolten alloy is driven off from the cooling roll(s) at the moment itcomes into contact therewith, and thus the molten metal is notsufficiently quenched by the cooling roll(s) so that the ratio ofequi-axed crystals is increased. As a result, the columnar structurehaving the area ratio of 50% in the thickness direction thereof cannotbe obtained, any way.

Further, the quenching rate for rapidly quenching the molten alloy ispreferably 1800° C./sec. or higher as described above. When thequenching rate is less than 1800° C./sec., the formation of the columnarstructure with the special shape as described above is impossible. Thequenching rate is preferably set to 2000° C./sec. or higher and morepreferably to 2400° C./sec. or higher.

The above rapidly-quenching process of the molten metal is preferablyexecuted in an inert gas atmosphere of Ar or He and in particular invacuum to prevent the deterioration of the molten alloy by oxidation.That is, when the rapidly-quenching process is executed in the inert gasatmosphere, an inert gas may be rolled in between the cooling roll(s)and the molten alloy, and thus the conditions for achieving a sufficientquenching effect is narrowed. On the other hand, when the processing isexecuted in vacuum, the inert gas is not rolled in on the contrary tothe case described above, and thus the molten metal is sufficientlyquenched on the surface of the cooling roll(s).

Further, a material such as Cu group alloy, Fe group alloy, Ni groupalloy or the like excellent in thermal conductivity is used as thematerial constituting the cooling roll. Further, a cooling roll composedof the above material and having a surface hardened by the formation ofCr plating or the like may be used.

Further, quartz generally used conventionally may be used as thematerial for constituting the crucible for preparing the molten alloy. Aquartz crucible, however, has a drawback in that since it does notproduce heat when heated by high frequency induction heating, the moltenmetal is cooled by the quartz when passing through the outlet of thecrucible and thus the outlet is liable to be closed. The closing of theoutlet can be effectively prevented by using a crucible formed ofceramics of such as Ti-boride or the like excellent in heatconductivity.

Since the hydrogen-absorbing alloy prepared by the abovemolten-metal-rapidly-quenching method has a fine crystal structure and aless amount of segregations of Mn or the like, when a negative electrodeis formed of it, the electrode capacity may be improved to the level of240 mAh/g or more and cycle life characteristics to the level of 500cycles or more at the same time. Further, the inventors have found fromthe experiment that a hydrogen-absorbing alloy for battery having moreexcellent characteristics can be obtained by removing the internaldistortion of the alloy produced by the rapidly-quenching processing, bypaying attention to the internal distortion.

Thus, in the present invention, the above internal distortion is removedby subjecting the hydrogen-absorbing alloy with the above compositionprepared by the molten-alloy-rapidly quenching processing to a heattreatment at a relatively low temperature of 200°-500° C. for one houror longer. More specifically, as a result of the further studies of theinventors, a new knowledge has been obtained that the capacity and lifeof the hydrogen-absorbing alloy of the present invention prepared at theaforesaid quenching rate of 1800° C./sec. are further improved togetherby being subjected to the heat treatment.

When the heat treatment temperature is less than 200° C., the internaldistortion is difficult to be removed, whereas when it exceeds 500° C.,the composition of the alloy is changed by the evaporation of the alloycomponents such as Mn and the like or an alloy strength is lowered by asecondary recrystallization. Therefore, the heat treatment temperatureis set to the range of 200°-500° C. In particular, the range of250°-350° C. is preferable to improve electrode characteristics.

Further, when the heat treatment time is shorter than one hour, theeffect for removing the internal distortion is reduced. On the otherhand, when the heat treatment is executed for a longer time, there is apossibility that the size of crystal particles is increased and thus theheat treatment time is preferably about 2-5 hours by taking amanufacturing effect into consideration.

Note, the heat treatment atmosphere is preferably composed of an inertgas or vacuum to prevent the oxidation of the hydrogen-absorbing alloyat a high temperature.

As described above, the internal distortion of the hydrogen-absorbingalloy can be effectively removed by the heat treatment of the alloyeffected at the relatively low temperature while keeping the homogeneitythereof, and thus the electrode capacity and life can be furtherextended. In particular, although the effect of the heat treatment islow in a rapidly-quenched molten alloy having a composition notcontaining Mn, when the rapidly-quenched molten alloy of the presentinvention having the composition containing Mn is subjected to the heattreatment, the electrode capacity and battery life thereof can begreatly improved together.

Next, a fourth hydrogen-absorbing alloy of the present invention forachieving the above second object will be described.

At least 90 wt % of the fourth hydrogen-absorbing alloy of the presentinvention is composed of AB_(x) of single phase where, A is at least onekind of element selected from rare earth elements including Y (yttrium),B is a metal mainly composed of Ni and at least one kind of elementselected from Co, Al, Fe, Si, Cr, Cu, Mn, Ti, Zr, Zn, Hf, V, Nb, Ta, Mo,W, Ag, Pd, B, Ga, In, Ge and Sn, 5.05≦x≦6!.

At least 90% of the fourth hydrogen-absorbing alloy for battery of thepresent invention must have the single phase composed of the AB_(x). Ifa phase (for example, phases composed of B, AB, AB₂, AB₃, A₂ B₇, AB₅,AB₁.4 and the like hereinafter referred to a second phase!) other thanthe above phase composed of AB_(x) exceeds 10 wt % in the alloy, thereare increased chances in which two or more kinds of alloy phases havinga different composition come into contact with each other. Theboundaries of the alloy phases having the different composition have aweak mechanical strength and cracks are liable to be formed from theseboundaries as hydrogen is absorbed and released.

Further, segregations are liable to be produced to the boundaries andthe alloy is liable to be corroded from the segregations. Further, thesecond phase absorbs a less amount of hydrogen as compared with AB_(x)when used as an electrode, and thus when an alloy including the secondphase in an amount exceeding 10 wt % is used as electrode, the electrodecapacity per a unit volume is reduced.

Further, the reason why the value of x is limited is as follows. When xis less than 5.05, a hydrogen-absorbing alloy which is less corrodedwhen battery is charged/discharged and difficult to be cracked andpulverized cannot be obtained. On the other hand, when x exceeds 6, thecreation of the second phase is admitted in the alloy making methodwhich can be usually employed in the industry and thus thecharacteristics of the hydrogen-absorbing alloy cannot be improved.

A constituting the AB_(x) (5.05≦x≦6) shows at least one kind selectedfrom rare earth elements including Y (specifically, Y, La, Ce, Pr, Nd,Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Lu).

Further, the element B shows a metal mainly composed of Ni and at leastone kind selected from Co, Al, Fe, Si, Cr, Cu, Mn, Ti, Zr, Zn, Hf, V,Nb, Ta, Mo, W, Ag, Pd, B, Ga, In, Ge and Sn. In the present invention,so long as the crystal system of the alloy maintains a CaCu₅ system, thetype of crystals is not a problem, but it preferably forms columnarstructure.

When a hydrogen-absorbing alloy for battery is made from a molten alloyhaving the composition exhibiting AB_(x) by the method of manufacturingthe hydrogen-absorbing alloy according to the present invention by usingvarious kinds of molten-metal-rapidly-quenching methods, the aforesaidhydrogen-absorbing alloy can be stably obtained, and thus thismanufacturing method is suitable. The molten-metal-rapidly-quenchingmethod includes the above rotating disk method, single roll method,double roll method, gas atomizing method and the like.

Next, a secondary nickel-metal hydride battery (cylindrical secondarynickel-metal hydride battery) according to the present invention usingthe above first to fourth hydrogen-absorbing alloys as a negativeelectrode activating material will be described below with reference toFIG. 3.

A hydrogen-absorbing alloy electrode (negative electrode) 11 containingthe hydrogen-absorbing alloy is wound with a non-sintering type nickelelectrode (positive electrode) 12 to a spiral-shape with a separator 13disposed therebetween and contained in cylindrical container 14 having abottom. An alkaline battery electrolyte is contained in the container14.

A disc-shaped opening seal plate 16 having a hole 15 defined at thecenter thereof is disposed on the upper opening of the container 14. Aring-shaped insulating gasket 17 is interposed between the peripheraledge of the seal plate 16 and the inner surface of the upper opening ofthe container 14 to fix the opening seal plate 16 to the container 14 ina gas-tight state through the gasket 17 by narrowing the diameter of theabove upper opening inwardly by caulking. A positive electrode lead 18has an end connected to the positive electrode 12 and the other endconnected to the lower surface of the opening seal plate 16. Ahat-shaped positive electrode terminal 19 is mounted on the opening sealplate 16 to cover the hole 15. A rubber safety valve 20 is disposed inthe space surrounded by the opening seal plate 16 and positive electrodeterminal 19 to close the hole 15. An insulating tube 21 is attached tothe vicinity of the upper end of the container 14 to fix the positiveelectrode terminal 19 and a collar 22 disposed on the upper end of thecontainer 14.

The above hydrogen-absorbing alloy electrode 11 includes a paste typeand a non-paste type as described below:

(1) a paste type hydrogen-absorbing alloy electrode is made in such amanner that a hydrogen-absorbing alloy powder obtained by pulverizingthe above hydrogen-absorbing alloy, a polymer binder and an electricconductive powder added when necessary are mixed to make a paste and thepaste is coated to and filled with an electric conductive substrate as acollector and dried and then pressed by a roller press or the like; and

(2) a non-paste type hydrogen-absorbing alloy electrode is made in sucha manner that the hydrogen-absorbing alloy powder, polymer binder andelectric conductive powder added when necessary are stirred anddispersed to the electric conductive substrate as a collector and thenpressed by a roller press or the like.

As a method of pulverizing the hydrogen-absorbing alloy, there areemployed a mechanical pulverizing method effected by a ball mill,pulverizer, jet mill or the like and a method of causing thehydrogen-absorbing alloy to absorb/release high pressure hydrogen andpulverizing the same by the expansion of the volume thereof at the time.

The polymer binder includes, for example, sodium polyacrylate,polytetrafluoroethylene (PTFE), carboxymethyl cellulose (CMC), polyvinylalcohol (PVA) and the like. Each of these polymer binders in the rangeof 0.5-5 weight parts is preferably combined with 100 weight parts ofthe hydrogen-absorbing alloy. When, however, the non-paste typehydrogen-absorbing alloy electrode of the above item (2) is to be made,polytetrafluoroethylene (PTFE) is preferably used as the polymer binderbecause PTFE is made to fibers by being stirred and can fix thehydrogen-absorbing alloy powder and the electric conductive powder addedwhen necessary to a three-dimensional state (mesh-state).

The electric conductive powder includes, for example, a carbon powdersuch as a graphite powder, ketchen black and the like and a metal powdersuch as a nickel powder, copper powder, cobalt powder and the like. Eachof these electric conductive powders in the range of 0.1-5 weight partsis preferably combined with 100 weight parts of the hydrogen-absorbingalloy.

The electric conductive substrate includes, for example, atwo-dimensional substrate such as a punched metal, expanded metal, wirenet and the like and a three-dimensional substrate such as a foamedmetal substrate, net-shaped sintered fiber substrate, plated-feltsubstrate composed of a non-woven fabric to which metal is plated, andthe like. When, however, the non-paste type hydrogen-absorbing alloyelectrode of the above item (2) is made, the two-dimensional substrateis preferably used as the electric conductive substrate because acombined material containing the hydrogen-absorbing alloy powder isdispersed.

The non-sintering type nickel electrode 12 combined with thehydrogen-absorbing alloy electrode is made in such a manner that a pasteis prepared by suitably combining the mixture of nickel hydroxide,cobalt hydroxide (Co(OH)₂) added when necessary and cobalt monoxide(CoO), metallic cobalt and the like with polyacrylate such ascarboxymethyl cellulose (CMC), sodium polyacrylate and the like, and thepaste is filled with the three-dimensional substrate such as the foamedmetal substrate, net-shaped sintered fiber substrate, plated-feltsubstrate composed of the non-woven fabric to which metal is plated, andthe like and dried and then pressed by the roller press or the like.

A non-woven fabric composed of polymer fibers used as the separator 13includes simple polymer fibers such as nylon, polypropylene,polyethylene and the like and complex polymer fibers mixed with thesepolymer fibers.

Used as the alkali battery electrolyte is, for example, a 6N to 9Npotassium hydroxide solution or the potassium hydroxide solution mixedwith lithium hydroxide, sodium hydroxide or the like.

Next, a nickel-metal hydride battery achieving the third object of thepresent invention will be described.

In the secondary nickel-metal hydride battery according to the presentinvention, an alloy made by a molten-metal-rapidly-quenching method isused a hydrogen-absorbing alloy constituting a hydrogen-absorbing alloyelectrode. Further, the amount of the battery electrolyte of thesecondary nickel-metal hydride battery composed by using thehydrogen-absorbing alloy electrode is within the range of 0.4-1.8 ml/Ahwith respect to the capacity of the hydrogen-absorbing alloy electrodeand further the capacity ratio of an alloy in an uncharged state in thebattery discharged state of the hydrogen-absorbing electrode to thecapacity of a nickel electrode is set within the range of 1.1-2.0. Thehydrogen-absorbing alloy is made by the aforesaidmolten-metal-rapidly-quenching method such as the rotating disc method,single roll method, double roll method, gas atomizing method and thelike.

The reason why the amount of the battery electrolyte is limited to theabove range in the relationship with the hydrogen-absorbing alloyelectrode is as follows. When the amount of the battery electrolyte isless than 0.4 ml/Ah, the area in which the hydrogen-absorbing alloyelectrode is in contact with the battery electrolyte is reduced, andthus a smooth battery reaction is prevented and the capacity of thenickel electrode constituting the battery cannot be sufficientlyextracted, with the result of the reduction of the battery capacity.When the amount of the battery electrolyte exceeds 1.8 ml/Ah, thesurface of the hydrogen-absorbing alloy electrode is covered with anexcessive battery electrolyte and thus the smooth reduction of theoxygen gas evolved from the nickel electrode is prevented in anexcessively charged state. As a result, a battery inner pressure isincreased and battery characteristics are deteriorated together with theoperation of the safety valve.

The reason why the capacity ratio of an alloy in an uncharged state inthe battery discharged state of the hydrogen-absorbing electrode to thecapacity of a nickel electrode is set within the above range is asfollows. When the capacity ratio is less than 1.1, since the batterycapacity is limited by the capacity of the hydrogen-absorbing alloyelectrode, the battery inner pressure is increased at the end ofcharge/discharge operation unless a special charge/discharge method isemployed, and thus the battery characteristics are deteriorated togetherwith the operation of the safety valve. On the other hand, when thecapacity ratio exceeds 2.0, the battery internal pressure is slightlyincreased, because the volume of the vacant space in the battery isreduced as well as the volume occupied by the hydrogen-absorbingelectrode is increased in the battery container. As a result, the amountof the nickel electrode as a volume-limited electrode is reduced withreduction of the battery capacity.

The first to third hydrogen-absorbing alloys composed as described aboveare an AB₅ type alloy containing Mn as an essential element andexcellent in the cycle life and initial characteristics with a highcapacity, and further can provide the negative electrode material with astable charging potential for nickel-hydrogen battery. These alloys canbe obtained by rapidly quenching a molten alloy having a predeterminedcomposition at a quenching rate of 1800° C./sec. or higher.

In addition, when thus prepared alloy is further subjected to a heattreatment at a relatively low temperature of about 200°-500° C., theinternal distortion of the alloy can be effectively eliminated whilekeeping the homogeneity of the alloy, whereby there can also be provideda further improved nickel-metal hydride battery excellent in batterycharacteristics.

Although the reason why the first hydrogen-absorbing alloy with theabove crystal structure has the aforesaid excellent characteristics isnot clear, it is supposed to be resulted from the following operation.That is, in the columnar structure in which the crystals of thehydrogen-absorbing alloy are grown in the same direction, the alloy isexpanded and shrank in a given direction as it absorbs and releaseshydrogen, and thus the pulverization of the alloy is suppressed by thereduction of the stress in the alloy. As a result, since the increase ofthe area of the alloy in contact with the battery electrolyte issuppressed, the corrosion of the alloy is prevented. Further, in thehydrogen-absorbing alloy made by the conventional casting method,segregations are dispersed to particle boundaries from which corrosionbegins.

It is supposed, however, that in the columnar structure having crystalsgrown from the quenched surface in the same direction as in the case ofthe present invention, the segregations of elements are concentrated tothe particular locations of the alloy as the crystals are grown, andthus the locations from which corrosion begins are reduced. Therefore,the cycle characteristics of the secondly nickel-metal hydride batteryto which the electrode containing the hydrogen-absorbing alloy isassembled are greatly improved.

The dispersion of a Mn concentration with respect to the secondhydrogen-absorbing alloy according to the present invention will bedescribed. An alloy, in which the maximum value of the Mn concentrationsdistributed therein exhibits a value exceeding 1.3 times the averagevalue of the Mn concentrations in the entire alloy, has the locations inwhich partially large Mn concentrations are dispersed in the alloy. Whenthe alloy is used to the negative electrode of the nickel-metal hydridebattery, a corrosion reaction is liable to be caused in these locationsand the thus the deterioration of the hydrogen-absorbing alloy itself isliable to be progressed.

Further, since the degree of expansion/shrinkage of thehydrogen-absorbing alloy volume caused by the hydrogenabsorption/release due to an electrode reaction is made partiallydifferent by the existence of the locations having the different Mnconcentrations, stress is produced in the alloy and pulverization isliable to be progressed to thereby increase a specific surface area, andthus the deterioration of the hydrogen-absorbing alloy is furtheraccelerated.

The above phenomenon is difficult to be caused in an alloy in which themaximum value of the Mn concentrations distributed therein exhibits avalue of 1.3 times or less the average value of the Mn concentrations inthe entire alloy. Therefore, it is supposed that when this alloy isapplied to a negative electrode, the progress of corrosion of the alloyis suppressed so that the cycle life characteristics of the nickel-metalhydride battery are improved.

Next, the maximum diameter of Mn segregations according to the thirdhydrogen-absorbing alloy of the present invention will be described.When an alloy, in which the maximum diameter of Mn segregations exceeds0.5 micron, is used to the nickel-metal hydride battery, a corrosivereaction begins from the segregations because a segregated portion has alarge size, and thus the deterioration of the hydrogen-absorbing alloyitself is liable to be progressed. Further, when the alloy isexpanded/shrank by the hydrogen absorption/release due to an electrodereaction, since stress is concentrated to the segregated points of Mn,cracks are liable to be made from the segregated points to therebyfurther accelerate pulverization.

On the other hand, the above phenomenon is difficult to be caused in ahydrogen-absorbing alloy in which the maximum diameter of Mnsegregations is 0.5 micron or less. Therefore, it is supposed that whenthis alloy is applied to the negative electrode of a nickel-metalhydride battery, the progress of corrosion of the negative electrodealloy is suppressed so that the cycle life characteristics of thenickel-metal hydride battery are improved.

Further, when the fourth hydrogen-absorbing alloy according to thepresent invention at least 90 wt % of which is composed of AB_(x) ofsingle phase where, A is at least one kind of element selected from rareearth elements including Y (yttrium), B is a metal mainly composed of Niand at least one kind of element selected from Co, Al, Fe, Si, Cr, Cu,Mn, Ti, Zr, Zn, Hf, V, Nb, Ta, Mo, W, Ag, Pd, B, Ga, In, Ge and Sn,5.05≦x≦6! is used as an activating material to form an electrode and abattery is arranged by using the electrode, a corrosion resistance to athick alkaline battery electrolyte can be greatly improved. As a result,a secondary alkaline battery (e.g., secondary nickel-metal hydridebattery) in which characteristics such as a cycle life and the like areimproved can be realized.

Although the reason why the hydrogen-absorbing alloy with the alloycomposition of the AB_(x) of the single phase has the excellentcorrosion resistance is not clear, this is supposed to be resulted fromthe following behavior.

That is, in a hydrogen-absorbing alloy whose crystal structure is foundnot to include a CaCu₅ type single phase but include a plurality ofphases in an amount of 10 wt % or more when observed by an X-raydiffraction, there are increased chances in which alloy phases having adifferent composition come into contact with each other. The boundariesbetween the alloy phases having the different composition have a weakmechanical strength and cracks are liable to be made from the boundariesas hydrogen is absorbed/released. Further, corrosion is liable to bemade to the boundaries due to segregations. Further, corrosion is liableto be made to the boundaries by the segregations. In addition, thephases having a composition other than AB_(x) absorb a less amount ofhydrogen ions as compared with the phase having AB_(x) when used as anelectrode. As a result, when the secondary nickel-metal hydride batteryto which the electrode containing the hydrogen-absorbing alloy as theactivating material is assembled is evaluated, not only the improvementof life is not admitted but also the reduction of capacity is admitted.

From the mentioned above, when at least 90 wt % of thehydrogen-absorbing alloy is composed of the AB_(x) of the single phase,cracks and corrosion can be suppressed and life can improved when thealloy is used as electrode. Further, since a hydrogen-absorbing alloyhaving a non-stoichiometric composition, although the crystal structurethereof is the CaCu₅ type, makes distortion in crystals, the alloyendures the expansion/shrinkage due to hydrogen absorption/release andas a result it can extend a cycle life of the electrode. Further,hydrogen is smoothly dispersed. As a result, when thishydrogen-absorbing alloy is assembled to battery, it has an effect toimprove large current discharge characteristics.

On the other hand, the hydrogen-absorbing alloy made by themolten-metal-rapidly-quenching method can homogenize a composition aswell as pulverize a crystal size and further suppress solidification andsegregation when the alloy is quenched as compared with thehydrogen-absorbing alloy made by the conventional method of melting amaterial in a crucible in an inert gas atmosphere or vacuum and thencasing the same to a casting mold. As a result, when an electrode isformed by using the hydrogen-absorbing alloy as an activating materialand a battery is arranged by using the electrode, a speed of corrosioncaused by an alkaline battery electrolyte can be reduced.

When the secondary nickel-metal hydride battery is arranged by using thenegative electrode containing the hydrogen-absorbing alloy made by themolten-metal-rapidly-quenching method, however, there is a case whereinwhen a battery design similar to that applied to the alloy made by theconventional method is used, not only the feature of thehydrogen-absorbing alloy made by the molten-metal-rapidly-quenchingmethod cannot not be exhibited but also particularly when the amount ofa battery electrolyte is excessively large, even the batterycharacteristics of the alloy made by the conventional method cannot bereproduced.

From the mentioned above, the secondary nickel-metal hydride batteryaccording to the present invention can achieve a smooth battery reactionand sufficiently extract the capacity of a nickel electrode to therebyimprove a capacity by limiting the amount of the battery electrolytewithin the range of 0.4-1.8 ml/Ah to the capacity of ahydrogen-absorbing alloy negative electrode. Furthermore, oxygen gasproduced from the nickel electrode in an excessively charged state canbe smoothly reduced, whereby the increase of the battery internalpressure can be suppressed.

Further, the battery capacity is avoided from being limited by thecapacity of the hydrogen-absorbing alloy electrode in such a manner thatthe capacity ratio of an alloy in an uncharged state in the batterydischarged state of the hydrogen-absorbing electrode to the capacity ofa nickel electrode is set within the range of 1.1-2.0 and the increaseof the battery internal pressure at the ends of charge and discharge canbe restricted without the need of using a special charge/dischargemethod. Simultaneously, the volume occupied by the hydrogen-absorbingalloy electrode in the battery container can be reduced. Correspondingto the reduced volume, a volume of the nickel electrode as avolume-limited electrode can be increased, thereby to increase thebattery capacity.

Accordingly, there can be provided a secondary nickel-metal hydridebattery having a high capacity and a long cycle life at a low cost, thebattery utilizing the characteristics of the hydrogen-absorbing alloymanufactured by molten-metal-rapidly-quenching method, and enabling tosuppress the increase of the battery internal pressure.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a schematic diagram showing a molten-metal-rapidly-quenchingapparatus using a single roll method;

FIG. 2 is a schematic diagram showing amolten-molten-metal-rapidly-quenching apparatus using a double rollmethod;

FIG. 3 is a perspective view showing an example of the arrangement of anickel-metal hydride battery according to the present invention;

FIG. 4 is a photograph taken by an electron microscope to show the metalstructure of a flake-shaped hydrogen-absorbing alloy subjected to amolten-molten-metal-rapidly-quenching processing;

FIG. 5 is a photograph taken by an electron microscope to show the metalstructure of hydrogen-absorbing alloy particles contained in a negativeelectrode taken out from a battery;

FIG. 6 is a photograph taken by an electron microscope to show the metalstructure of hydrogen-absorbing alloy particles contained in thenegative electrode taken out from the battery;

FIG. 7 is a photograph taken by an electron microscope to show the metalstructure of hydrogen-absorbing alloy particles contained in thenegative electrode taken out from the battery;

FIG. 8 is a photograph taken by an electron microscope to show the metalstructure of hydrogen-absorbing alloy particles contained in thenegative electrode taken out from the battery;

FIG. 9 is a photograph taken by an electron microscope to show the metalstructure of the hydrogen-absorbing alloy according to an embodiment 9B;

FIG. 10 is a schematic diagram copying the columnar structure of themetal structure shown in FIG. 9;

FIG. 11 is a schematic diagram showing the columnar structure having anaspect ratio of 1:5 or higher in the metal structure shown in FIG. 9;

FIG. 12 is a schematic diagram showing the columnar structure having anaspect ratio of 1:4 or higher in the metal structure shown in FIG. 9;

FIG. 13 is a schematic diagram showing the columnar structure having anaspect ratio of 1:3 or higher in the metal structure shown in FIG. 9;

FIG. 14 is a schematic diagram showing the columnar structure having anaspect ration of 1:2 or higher in the metal structure shown in FIG. 9;

FIG. 15 is a photograph taken by an electron microscope to show themetal structure of the hydrogen-absorbing alloy according to anembodiment 5A;

FIG. 16 is a schematic diagram copying the columnar structure of themetal structure shown in FIG. 15;

FIG. 17 is a schematic diagram showing the columnar structure having anaspect ratio of 1:5 or higher in the metal structure shown in FIG. 15;

FIG. 18 is a schematic diagram showing the columnar structure having anaspect ratio of 1:4 or higher in the metal structure shown in FIG. 15;

FIG. 19 is a schematic diagram showing the columnar structure having anaspect ratio of 1:3 or higher in the metal structure shown in FIG. 15;

FIG. 20 is a schematic diagram showing the columnar structure having anaspect ratio of 1:2 or higher in the metal structure shown in FIG. 15;

FIG. 21 is a photograph taken by an electron microscope to show themetal structure of the hydrogen-absorbing alloy according to anembodiment 12A;

FIG. 22 is a schematic diagram copying the columnar structure of themetal structure shown in FIG. 21;

FIG. 23 is a schematic diagram showing the columnar structure having anaspect ratio of 1:5 or higher in the metal structure shown in FIG. 21;

FIG. 24 is a schematic diagram showing the columnar structure having anaspect ratio of 1:4 or higher in the metal structure shown in FIG. 21;

FIG. 25 is a schematic diagram showing the columnar structure having anaspect ratio of 1:3 or higher in the metal structure shown in FIG. 21;

FIG. 26 is a schematic diagram showing the columnar structure having anaspect ratio of 1:2 or higher in the metal structure shown in FIG. 21;

FIG. 27 is a photograph taken by an electron microscope to show themetal structure of the hydrogen-absorbing alloy according to acomparative example 7B;

FIG. 28 is a characteristic diagram showing the relationship between thediameter of crystal particles of a hydrogen absorbing alloy and thecycle life of the battery;

FIG. 29 is a characteristic diagram showing the relationship between theratio of the maximum value to the average value of the Mn concentrationin an alloy and the cycle life of the battery;

FIG. 30 is a characteristic diagram showing the relationship between themaximum diameter of the Mn particles segregated in an alloy and thecycle life of the battery;

FIG. 31 is a characteristic diagram showing the relationship between thecomposition ratio x, electrode capacity, and the cycle life in anembodiment 19;

FIG. 32 is a schematic cross sectional view showing an apparatus formaking hydrogen absorbing-alloy particles by a rotating disc method;

FIG. 33 is a schematic cross sectional view showing an apparatus formaking hydrogen absorbing-alloy particles by a gas atomizing method;

FIG. 34 is a graph comparing cycle life of a battery resulting fromvarious capacity ratios of negative and positive electrode alloys andvarious amounts of a battery electrolyte;

FIG. 35 is a graph comparing the maximum values of a battery internalpressure resulting from various capacity ratios of negative and positiveelectrode alloys and various amounts of a battery electrolyte;

FIG. 36 is a graph comparing maximum battery capacities resulting fromvarious capacity ratios of negative and positive electrode alloys andvarious amounts of a battery electrolyte;

FIG. 37 is a graph showing the relationship between the charge/dischargecycle and the battery capacity of comparative examples 25, 26 and 27 andexamples 22, 23 and 24.

FIG. 38 is a graph showing the relationship between the charge/dischargecycle and the battery capacity of an AA type battery.

FIG. 39 is a graph showing the relationship between the charge/dischargecycle and the battery internal pressure of the AA type battery.

DESCRIPTION OF THE PREFERRED EMBODIMENTS

Embodiments of the present invention will be described below morespecifically.

Embodiments 1-9

Mixture of various law materials were prepared, taking the amount of thelaw materials lost when they were melted into consideration, so thatrapidly-quenched molten alloys obtained by being rapidly-quenched fromthe melt had the compositions shown in Table 1. The mixtures of thevarious law materials were put into a crucible made of Ti-boride andmelted by a high frequency induction heating method, and various moltenmetal alloys were prepared. Next, the thus obtained various molten metalalloys were injected onto the surface of the cooling roll of anapparatus employing a single roll method shown in FIG. 1 so thatflake-shaped rapidly-quenched molten alloys having a thickness of 50microns were prepared. The cooling roll was composed of a copper rollhaving a diameter of 300 mm and the distance between an injection nozzleand the cooling roll was set to 50 mm and an injection pressure was setto 0.02 Kgf/cm².

Further, the rapid quenching was executed in vacuum, the rotating speed(rpm) of the cooling roll was set to 600 rpm and an adjustment wasperformed so that the molten metal alloy had an average quenching rateof 2400° C./sec.

Next, the thus obtained respective rapidly-quenched molten alloys werepulverized and classified to 200 mesh or less so that hydrogenabsorbing-alloy powders for battery was prepared. Next, the thusprepared hydrogen absorbing-alloy powders for battery, PTFE powder andcarbon powder were weighed so that they were 95.5 wt %, 4.0 wt % and 0.5wt %, respectively and then kneaded so that respective electrode sheetswere made.

The electrode sheets were cut off to a predetermined size and attachedunder pressure to a nickel collector to make hydrogen absorbing-alloyelectrodes, respectively.

Then, the respective hydrogen absorbing-alloy electrodes were charged upto 300 mAh/g with a current (220 mA/g) per 1 g of alloy and dischargedwith the above current until a potential difference of -0.5 V wasachieved with respect to an Hg/HgO reference electrode and at this timea maximum electrode capacities were measured. The result of themeasurements is shown Table 1. Further, the number of activations of therespective electrodes was measured. The number of activations means thenumber of charge/discharge cycles necessary for the electrodes thus madeto exhibit a maximum capacity and serves as an index for determining thegood or bad rising-up of the battery characteristics of batteries madeby using these alloys.

On the other hand, a paste was prepared by adding a small amount of CMC(carboxymethyl cellulose) and water to 90 wt % of nickel hydroxide and10 wt % of cobalt monoxide and stirring and mixing them. This paste wasfilled to a porous nickel member having a three-dimensional structureand dried and rolled by a roller press to make a nickel electrode.

Then, AA type nickel-metal hydride batteries of the respectiveembodiments were assembled by combining the above respective hydrogenabsorbing-alloy electrodes and the nickel electrode. Here, the capacityof the respective batteries was set to 650 mAh as the theoreticalcapacity of the nickel electrode and a solution mixed with 7N potassiumhydroxide and 1N lithium hydroxide was used as a battery electrolyte.

Next, the respective batteries were charged with 650 mA for 1.5 hoursand repeatedly subjected to charge/discharge cycles so that a currentwas discharged at the current of 1A until the batteries had a voltage of1 V and the number of the cycles at which the capacity of the batteriesbecame 80% of an initial capacity was measured as a battery life.

Further, the respective batteries were assembled and charged 10 cyclesand then they were disassembled to analyze the metal structure of thehydrogen absorbing-alloys used as the negative electrodes. Note, thehydrogen absorbing-alloy powder assembled once into the battery wasintegrated with a polymer binder and the like and further partiallycorroded by the electrolyte and an etching solution used to observe afine structure, and thus it was difficult to observe the metal structurethereof as it was. Thus, specimens for analysis were made by theprocedures shown in the following items (1)-(3) and further the metalstructure of the specimens was analyzed by the method shown in item (4).

(1) Taking-Out of Negative Electrode

When the battery is disassembled in the state that it is not perfectlydischarged, there is a possibility that the hydrogen absorbing-alloycontained in the negative electrode may be fired, and thus thenickel-metal hydride battery is perfectly discharged and then thebattery is disassembled and the negative electrode is taken out. Toprevent the firing, the negative electrode taken out from the battery issufficiently washed with water and dried. If the negative electrode isnot sufficiently washed with water and dried, it is not in intimatecontact with a resin in the next resin burying process and may beexfoliated from the resin.

(2) Burying of Negative Electrode by Resin

Ten pieces of specimens of 10 mm×5 mm are cut off from the driednegative electrode and numbers from 1 to 10 were put to the specimens.Each of these specimens is vertically disposed in a mold so that longerside thereof is directed downward and a gap therebetween was filled witha resin flowed into it to form a composite member. A resin having a lowviscosity such as an epoxy resin is used as the resin to be buried.Further, it is preferable that the resin is flowed into the mold in thestate that the temperature thereof is increased to lower its viscosityso that the specimen is in intimate contact with the resin.

(3) Polishing of Composite Member

The surface of the cured composite member is polished by sequentiallyusing water resistant abrasive papers (#600)-(#1500) to expose the crosssection of the hydrogen absorbing alloy. This polishing operation may becarried out by a polishing machine. In this case, however, since thehydrogen absorbing-alloy in the electrode is liable to be exfoliated dueto an excessive impact force, it is preferable that the polishingoperation is manually carried out.

(4) Observation of Alloy Structure

When the metal structure of the hydrogen absorbing alloy contained inthe specimens is observed by a scanning type electron microscope (SEM),the metal structure may not be partially confirmed clearly because thehydrogen absorbing alloy is integrated with the polymer binder.Therefore, only the alloys whose metal structure can be clearlyrecognized are selected as the objects of the observation.

The observation was carried out by selecting a visual field in which themetal structure of the hydrogen-absorbing alloy exposed to the crosssection of the electrode could be observed as much as possible withinthe region R partitioned by a maximum rectangular shape in which thecrystal structure of the alloy integrally touched when the metalstructure is photographed by using the SEM at a magnification of, forexample, 1500-2000 as shown in FIGS. 10, 16 and 22, the above crystalstructure being a portion of the entire indefinite crystal structure inwhich crystal particles could be visually confirmed. At that time, withrespect to each of the hydrogen-absorbing alloys of the presentinvention contained in the negative electrode, the ratio of the crystalparticles having the aspect ratio of 1:2 or higher occupying in themetal structures which can be recognized is preferably 50% or higher,more preferably 70% or higher and further more preferably 80% or higher.This is because that when the ratio is less than 50%, a crystal particleboundaries are increased and as a result segregations are alsoincreased, and thus the alloy particles are greatly deteriorated.Further, it is necessary that the ratio of the number of the alloyparticles with crystal particles having the aspect ratio of 1:2 orhigher and the area ratio of the columnar of 50% or more is preferably30% or more, more preferably 50% or more and further more preferably 70%or more with respect to the number of the entire particles of thehydrogen-absorbing alloy having the metal structures which can bevisually recognized. When the ratio of the number of the crystalparticles is less than 30%, the number of the crystal particles liableto be deteriorated is relatively increased, and when a battery isformed, the life thereof is remarkably shortened.

The aspect ratio is the ratio of the minor diameter of a crystalparticle to the major diameter thereof, and the major diameter isdefined as the maximum length in the axial direction of the crystalparticle and the minor diameter as the maximum length in the directionperpendicular to the axis.

In the metal structure of the hydrogen-absorbing alloy according to thepresent invention, the columnar crystal particles preferably have anaverage minor diameter of 30 microns or less, more preferably 20 micronsor less and further more preferably 10 microns or less. When the averageminor diameter exceeds 30 microns, many segregations are produced andthe corrosion resistance of the alloy is lowered and the life thereof isshortened as well as a charge/discharge cycle is greatly lowered when abattery is made. Further, since the area of the crystal boundaries asthe moving paths of hydrogen in the alloy is reduced, the hydrogen hasan increased diffusion resistance and thus a battery voltage is liableto be lowered when a large current discharges.

Next, a method of determining the aspect ratio of the columnar structureconstituting the metal structure of the hydrogen-absorbing alloy will bespecifically described.

FIG. 4 is a photograph taken by an electron microscope to show anexample of the metal structure of the hydrogen-absorbing alloy accordingto this embodiment and the photograph shows the cross section in thethickness direction of a rapidly-quenched molten alloy in contact withthe cooling roll of the single roll apparatus. The hydrogen-absorbingalloy is a flake-shaped rapidly-quenched molten alloy before it ispulverized. In FIG. 4, the lower side of the cross section is a quenchedsurface in contact with the cooling roll and the upper side thereof is afree side. It can be clearly recognized the state that columnarstructure having various aspect ratios is vertically grown from thequenched surface by the molten-alloy-rapidly-quenching process.

However, the alloy obtained by pulverizing the flake-shapedrapidly-quenched molten alloy is used to the negative electrode of anactual battery and the pulverized powder of the alloy is sometimeseroded by a battery electrolyte, and thus even if the columnar structureis observed by the SEM, the columnar structure is not always clearlyobserved. The cases in which the metal structure is made unclear will bedescribed below with reference to FIGS. 5-8.

FIGS. 5-8 show the photographs taken by the SEM of thehydrogen-absorbing alloy contained in the negative electrode taken outfrom an actually used battery. More specifically, in FIG. 5, a crosssection in the vertical direction with respect to the quenching surfaceof the cooling roll is observed and the state that columnar structure isvertically grown can be recognized. FIG. 6 shows the surface structureof the free side opposite to the side in contact with the cooling roll(the roll side). In this case, since only the edge faces correspondingto the minor diameter of columnar structure is observed, the columnarstructure may be observed as if they were equi-axed crystals. In FIG. 7,although columnar structure is partially observed at the central portionthereof, since the right upper portion thereof is eroded by a batteryelectrolyte, it is difficult to clearly recognize a metal structure as awhole. FIG. 8 shows an example in which the upper surface (whiteportion) of a hydrogen-absorbing alloy is eroded by a batteryelectrolyte when observed by the SEM and a metal structure cannot beclearly recognized as a whole.

Thus, when the metal structure of the hydrogen-absorbing alloy containedin a negative electrode is to be observed, an object surface ismirror-polished and etched to expose the crystal boundaries of the metalstructure. When, however, an etching solution is not suitable to thecomposition of the hydrogen-absorbing alloy, the etching solutionexcessively erodes the entire alloy, and thus the crystal boundariescannot be clearly exposed. Therefore, even if columnar structure isformed, when they are greatly eroded, the recognition of the metalstructure as a whole is difficult to be recognized. On the other hand,even when they are slightly eroded, crystal particle boundaries aredifficult to be clearly recognized although the configuration of thecolumnar structure can be barely recognized visually. Note, in additionto the above cases, when a cross section perpendicular to the coolingroll is observed, columnar structure may observed as if they wereequi-axed crystals depending upon an angle between the surface of thecooling roll and the cross section. Therefore, in this case, anattention must be taken when the area ratio of the columnar structure ismeasured.

FIGS. 9, 15 and 21 show the photographs taken by the SEM of thehydrogen-absorbing alloy particles contained in the negative electrodetaken out from actually used batteries. The hydrogen-absorbing alloyparticles shown in FIGS. 9, 15 and 21 correspond to embodiments 5, 1 and8, respectively.

Although clear alloy particles in which columnar structure is grown areobserved as shown in the central portion of FIG. 15, the clear alloyparticles are also surrounded by alloy particles whose crystal structurecannot be clearly observed because they are eroded by the electrolyte ofa battery or an etching solution used to observe them with the SEM.

In particular, when the etching solution is not suitable to thecomposition of the hydrogen-absorbing alloy, the metal structure of thealloy cannot be observed because the surface of the alloy is eroded bythe etching solution.

A method of calculating the ratio of crystal particle having the aspectratio of 1:2 or higher occupying in the entire crystal particles basedon the above SEM photographs will be described. First, the number ofhydrogen-absorbing alloy particles whose metal structure can be clearlyobserved is counted in the entire alloy particles observed in the crosssection of a single polished piece of a negative electrode and the countvalue is represented by N1. At this time, a specific signal from an rareearth element is detected by using an X-ray microanalyzer (EPMA), energydispersion type X-ray analyzer (EDX) or the like to confirm that thealloy particles are composed of the hydrogen-absorbing alloy. When thisspecific signal is not detected from the rare earth element, the alloyparticles are assumed to be stuck materials such as pulverized piecesand determined not to be the hydrogen-absorbing alloy particles andexcluded from the number of the alloy particles.

Next, the number of the alloy particles N1' in which crystal particleshaving the aspect ratio of 1:2 or higher occupy 50% or more of the areaof the metal structure is counted in the N1 pieces of the alloyparticles. Hereinafter, the same count will executed to the respectivepieces of the specimens of the negative electrode.

The ratio of the columnar structure is calculated by substituting thusdetermined values of N1-N10 and N1'-N10' for the following equation.

    Ratio of columnar structure (%)=(N1'+N2' . . . +N10')/(N1+N2+ . . . +N10)×100

Next, a method of calculating the ratio of the columnar structureoccupying in the metal structure will be described. Note, the longcrystal particles having the aspect ratio of 1:2 were made to the objectto be investigated as the columnar structure. Further, not onlyequi-axed crystals but also chill crystals and various stuck materialswere included in the crystal particles having the aspect ratio of lessthan 1:2 . The area occupied by the columnar structure was measured byusing an image analyzer (Model LUZEX 500 made by Nippon Regulator Co.,Ltd.). More specifically, when description is made by using theembodiment 5 as an example, a thin tracing paper (basis weight: about 40g/m²) was placed on the SEM photograph of the metal structure shown inFIG. 9 and particle boundaries were copied to the tracing paper so thata copied paper as shown in FIG. 10 was created. In thehydrogen-absorbing alloy particles, an eroded portion 30 eroded by abattery electrolyte was formed on the left side of columnar structure31. Further, a stuck material 33 such as a fragment or the like of apulverized matter was located at the central portion of the region R.

Next, the portion corresponding to the columnar structure having theaspect ratio of 1:5 or higher was colored with black to obtain FIG. 11.Then, the portion corresponding to the columnar structure having theaspect ratio of 1:4 or higher was colored with black to obtain FIG. 12in the same way. Next, the portions having the aspect ratios of 1:3 and1:2 or higher were colored with black in the same way to obtain FIGS. 13and 14. Next, FIGS. 11-14 were subjected to an image processing by usingan image analyzer so that the area ratios of the columnar structurescorresponding to these aspect ratios were optically analyzed andcalculated. More specifically, the image analyzer recognized thepresence and absence of the columnar structure in the object range R bya shade of color and calculated the area ratios.

FIGS. 15-20 and FIGS. 21-26 show the examples in which the area ratio iscumulatively calculated with respect to other alloy structures. FIG. 15is an SEM photograph showing the hydrogen-absorbing alloy particlesaccording to the embodiment 1. The copy shown in FIG. 16 was obtained bytracing the crystal structure of the alloy particles at the centralportion which could be clearly recognized in the alloy particles shownin the SEM photograph of FIG. 15. In FIG. 16, the linear portion at theupper edge is an abutted face 34 abutted against a cooling roll and finechill crystals 35 made by the super-rapid quenching action of thecooling roll are located along the abutted face 34. Note, since thechill crystals 35 are fine, the crystal boundaries thereof are notshown. Further, a stuck material 33 is located on the right side of theregion R.

Next, the portions of the columnar structures having the aspect ratiosof 1:5 or higher, 1:4 or higher, 1:3 or higher and 1:2 or higher arecolored with black, respectively to obtain the copies shown in FIGS.17-20 in the same way as the embodiment 5.

The copy of FIG. 22 showing the crystal structure of thehydrogen-absorbing alloy according to the embodiment 8 was made from theSEM photograph shown in FIG. 21 in the same way and the columnarstructures corresponding to respective aspect ratios were colored withblack to make FIGS. 23-26 which were analyzed by the image analyzer todetermine the area ratios of the columnar structure portions.

As apparent from FIGS. 9-26, it was confirmed that columnar structures31 were sufficiently grown in any of the crystal structures, whereasequi-axed crystals 32 partially existed in the structures.

Note, as shown in FIGS. 10, 16 and 22, the region subjected to the aboveanalysis was limited to the region R partitioned by a maximumrectangular shape in which the crystal structure of the alloy integrallytouched in the entire indefinite crystal structure in which crystalparticles could be visually confirmed. Note, the columnar structurelocated on the boundary of the region R employed the area thereoflocated only in the region R and the aspect ratios of them were assumedfrom the entire configuration of the columnar structures including theirportions located to the outside of the region.

Table 1 shows the area ratio and minor diameter of the columnarstructure of the respective hydrogen-absorbing alloys according to theembodiments 1-9, the maximum electrode capacity of the electrodes andthe activation number of the electrodes using the hydrogen-absorbingalloys, and the number charge/discharge cycles of the batteries.

                                      TABLE 1                                     __________________________________________________________________________                                                      Characteristics                                      Area Ratio of Columnar Structures                                                                 Minor         Number                                  RPM of                                                                            Aspect Ratio        Dia of        of                                 Manu-                                                                              Cooling                                                                           1:2 1:3 1:4 1:5     Columnar                                                                           Electrode                                                                          Cycle                                                                             Acti-              Specimen        facturing                                                                          Roll                                                                              or  or  or  or  As a                                                                              Structures                                                                         Capacity                                                                           Life                                                                              vation             No.  Alloy Composition                                                                        Method                                                                             (r.p.m)                                                                           higher                                                                            higher                                                                            higher                                                                            higher                                                                            whole                                                                             (μm)                                                                            (mAh/g)                                                                            (cycles)                                                                          (times)            __________________________________________________________________________    Embodi-                                                                            LmNi.sub.4.0 Co.sub.0.4 Mn.sub.0.3 Al.sub.0.3                                            Single                                                                             600 95  89  82  71  59  2.5  259  612 3                  ment 1          Roll                                                                          Method                                                        Embodi-                                                                            LmNi.sub.3.6 Co.sub.0.4 Mn.sub.0.5 Al.sub.0.3                                            Single                                                                             600 97  89  78  75  66  2.3  263  557 2                  ment 2          Roll                                                                          Method                                                        Embodi-                                                                            LmNi.sub.4.0 Co.sub.0.4 Mn.sub.0.3 Cr.sub.0.3                                            Single                                                                             600 96  88  82  79  68  2.3  256  575 3                  ment 3          Roll                                                                          Method                                                        Embodi-                                                                            LmNi.sub.4.0 3.6Co.sub.0.4 Mn.sub.0.5 Cr.sub.0.5                                         Single                                                                             600 95  91  88  85  71  2.3  264  544 2                  ment 4          Roll                                                                          Method                                                        Embodi-                                                                            LmNi.sub.4.2 Mn.sub.0.5 Cu.sub.0.8                                                       Single                                                                             600 97  91  89  83  62  2.6  261  548 2                  ment 5          Roll                                                                          Method                                                        Embodi-                                                                            LmNi.sub.4.2 Mn.sub.0.8                                                                  Single                                                                             600 96  92  87  84  73  2.7  271  539 2                  ment 6          Roll                                                                          Method                                                        Embodi-                                                                            LmNi.sub.4.4 Mn.sub.0.3 Al.sub.0.3                                                       Single                                                                             600 95  86  79  76  57  2.5  258  563 2                  ment 7          Roll                                                                          Method                                                        Embodi-                                                                            LmNi.sub.4.0 Co.sub.0.4 Mn.sub.0.3 Fe.sub.0.3                                            Single                                                                             600 97  96  95  87  68  2.4  250  579 2                  ment 8          Roll                                                                          Method                                                        Embodi-                                                                            LmNi.sub.4.0 Co.sub.0.4 Mn.sub.0.3 Si.sub.0.3                                            Single                                                                             600 95  89  86  81  64  2.2  247  548 2                  ment 9          Roll                                                                          Method                                                        __________________________________________________________________________

As apparent from Table 1, since each of the hydrogen-absorbing alloysfor battery according to the examples 1-9 prepared by rapidly quenchingthe molten alloys each having the predetermined composition added withMn has the columnar structure sufficiently grown in the alloy structurethereof and a very small amount of segregations of the elementsconstituting the alloy, when the alloys are used as a negative electrodematerial, an electrode capacity can be greatly improved withoutshortening a life.

Further, since a maximum electrode capacity can be achieved by the smallnumber of charge/discharge cycles or the small number of activationssuch as 2-3 cycles (times), the battery characteristics can be rapidlyrisen up at an initial time and the manufacturing cost of the batterycan be reduced.

Note, the metal structure of the respective hydrogen-absorbing alloypowders made in the embodiments 1-9 was analyzed according to theprocedures shown in the following items (A), (B) and the above item (4)before electrodes were made from the alloy powders.

(A) Burying of Resin

An alloy specimen was taken in an amount of 100 mg and dispersed to thecenter of a resin burying frame (made of polypropylene) with a diameterof 20 mm for SEM specimen.

Next, an epoxy resin (EPO-MIX made by Buller Ltd.) commerciallyavailable as a resin for burying a SEM specimen and a curing agent weresufficiently mixed and the thus obtained mixed material was poured intothe burying frame and cured. At that time, it was preferable to preheatthe resin to about 60° C. to lower the viscosity thereof or to removefoams therefrom by evacuating the resin in a vacuum desiccator after ithad been poured into the frame to improve the intimate contact propertyof the resin with the specimen.

(B) Polishing

Next, the specimen buried by the above procedure was polished by arotary polishing machine until it was mirror-polished. Since thespecimen of the hydrogen-absorbing alloy was liable to react with water,it was polished with water-resistant abrasive papers mounted on thepolishing machine rotating at 200 rpm while dropping methyl alcohol. Atthat time, the abrasive papers were sequentially changed to finer onesof #180, #400 and #800. Then, the specimen was mirror-polished by thediamond paste on the rotary polishing machine having a felt set thereon,the felt being provided with the diamond paste whose grain size was madefiner in the sequence of 15 microns, 3 microns and 0.25 micron.

The area ratios and minor diameters of the columnar structures of thehydrogen-absorbing alloys contained in the respective specimens obtainedby the above procedures were measured by the method shown in the aboveitem (4). As a result, it was confirmed that the hydrogen-absorbingalloys according to the embodiments 1-9 exhibited values substantiallyequal to the respective measured values (Table 1) of the columnarcrystals of the alloy contained in the negative electrode taken from anickel-hydrogen battery charged and discharged 10 cycles.

Embodiment 10

An ingot of AB₅ type hydrogen-absorbing alloy in the weight of 200 g wasprepared by adjusting the composition thereof by taking an amount of alaw material lost when it was melted into consideration, so that arapidly-quenched molten alloy obtained by being quenched by amolten-metal-rapidly-quenching method had the composition of LmNi₄.0Co₀.4. Mn₀.3 Al₀.3 (Lm is composed of a La-rich misch metal containingCe: 3 wt %, La: 50 wt %, Nd: 40 wt %, Pr: 5 wt %, and other rare earthelements: 2 wt %) and the thus obtained ingot was melted in a highfrequency induction heating furnace to prepare a molten alloy. Next, aflake-shaped rapidly-quenched molten alloy having a thickness of 50microns was prepared by dropping the thus obtained molten alloy onto thesurface of the cooling roll of the apparatus employing the single rollmethod shown in FIG. 1.

The rapidly-quenched molten alloy was subjected to a heat treatment inan argon atmosphere at the temperature of 300° C. for 4 hours and thenpulverized, classified to 200 mesh or less and made to ahydrogen-absorbing alloy powder for battery alloy powder (A)!.

On the other hand, a rapidly-quenched molten alloy was prepared in thesame way as the alloy powder (A) and subjected to a heat treatment for 4hours at the temperatures set to 150° C., 200° C., 250° C., 350° C.,400° C., 500° C., 550° C. and 600° C., respectively, classified to 200mesh or less and made to alloy powders (B)-(I). Further, the alloypowder (A) subjected to a heat treatment for 0.5 hour, 1 hour and 6hours, respectively was made to powders (J)-(L).

On the other hand, for comparison, a rapidly-quenched molten alloy wasprepared in the same way as the alloy powder (A), classified to 200 meshor less and made to an alloy powder (M) without being to a heattreatment.

Table 2 shows the composition of the respective alloy powders (A)-(L)having being subjected to the heat treatment and the composition of thealloy powder (M) not subjected to the heat treatment.

                                      TABLE 2                                     __________________________________________________________________________             Heat Treatment Conditions                                                     Temperature                                                                         Time                                                           Specimen (°C.)                                                                        (Hr)                                                                             Atmosphere                                                                          Alloy Composition After Heat Treatment                __________________________________________________________________________    Alloy Powder (A)                                                                       300   4  Ar    Lm.sub.0.96 Ni.sub.4.00 Co.sub.0.41 Mn.sub.0.29                               Al.sub.0.31                                           Alloy Powder (B)                                                                       150   4  Ar    Lm.sub.0.97 Ni.sub.4.00 Co.sub.0.41 Mn.sub.0.30                               Al.sub.0.30                                           Alloy Powder (C)                                                                       200   4  Ar    Lm.sub.0.96 Ni.sub.4.00 Co.sub.0.41 Mn.sub.0.30                               Al.sub.0.31                                           Alloy Powder (D)                                                                       250   4  Ar    Lm.sub.0.96 Ni.sub.4.00 Co.sub.0.41 Mn.sub.0.30                               Al.sub.0.30                                           Alloy Powder (E)                                                                       350   4  Ar    Lm.sub.0.97 Ni.sub.4.00 Co.sub.0.40 Mn.sub.0.30                               Al.sub.0.30                                           Alloy Powder (F)                                                                       400   4  Ar    Lm.sub.0.97 Ni.sub.4.00 CO.sub.0.40 Mn.sub.0.29                               Al.sub.0.30                                           Alloy Powder (G)                                                                       500   4  Ar    Lm.sub.0.96 Ni.sub.4.00 CO.sub.0.40 Mn.sub.0.29                               Al.sub.0.31                                           Alloy Powder (H)                                                                       550   4  Ar    Lm.sub.0.93 Ni.sub.4.00 CO.sub.0.41 Mn.sub.0.27                               Al.sub.0.30                                           Alloy Powder (I)                                                                       600   4  Ar    Lm.sub.0.91 Ni.sub.4.00 CO.sub.0.42 Mn.sub.0.26                               Al.sub.0.31                                           Alloy Powder (J)                                                                       300   0.5                                                                              Ar    Lm.sub.0.98 Ni.sub.4.00 Co.sub.0.40 Mn.sub.0.30                               Al.sub.0.30                                           Alloy Powder (K)                                                                       300   1  Ar    Lm.sub.0.98 Ni.sub.4.00 CO.sub.0.41 Mn.sub.0.30                               Al.sub.0.31                                           Alloy Powder (L)                                                                       300   6  Ar    Lm.sub.0.97 Ni.sub.4.00 CO.sub.0.40 Mn.sub.0.30                               Al.sub.0.29                                           Alloy Powder (M)                                                                       --    -- Ar    Lm.sub.0.98 Ni.sub.4.00 Co.sub.0.40 Mn.sub.0.31                               AL.sub.0.30                                           __________________________________________________________________________

As apparent from the result shown in Table 2, the alloy powder (M) notsubjected to the heat treatment exhibits substantially a desiredcomposition. Further, a large variation in the composition is notadmitted in the alloy powders (A)-(G) and (J)-(L) having been subjectedto the heat treatment in the temperature range of from 150° C. to 500°C. On the other hand, the alloy powders (H) and (I) exhibit a largevariation of the composition because they are subjected to the heattreatment at a little higher temperature and thus the rare earthelements and Mn which are liable to be evaporated are reduced in alittle large amount. Since the composition of the alloys is liable to bechanged when they are subjected to the heat treatment at a hightemperature, the heat treatment is preferably carried out in a lowtemperature range.

Next, any one of the thus prepared powders (A)-(M), PTFE powder andcarbon powder were weighed so that they were 95.5 wt %, 4.0 wt % and 0.5wt % and kneaded to prepare respective electrode sheets. The electrodesheets were cut off to a desired size and attached to a nickel collectorunder pressure to make hydrogen-absorbing alloy electrodes. Theelectrode made of the alloy powders (A)-(M) were referred to aselectrodes (A)-(M), respectively.

Then, the respective hydrogen absorbing-alloy electrodes (A)-(M) werecharged up to 300 mAh/g at a current value of 220 mA per 1 g of alloy(220 mA/g) and discharged with the above current value until a potentialdifference of -0.5 V was achieved with respect to an Hg/HgO referenceelectrode and at that time a maximum electrode capacity was measured.The result of the measurement is shown Table 3.

On the other hand, a paste was prepared by adding a small amount of CMC(carboxymethyl cellulose) and water to 90 wt % of nickel hydroxide and10 wt % of cobalt monoxide and stirring and mixing them. This paste wasfilled to a porous nickel member having a three-dimensional structureand dried and rolled by a roller press to make a nickel electrode.

Then, AA type nickel-metal hydride batteries were assembled by combiningthe above respective hydrogen absorbing-alloy electrodes (A)-(M) and thenickel electrode. Here, the battery using the alloy electrode (A) as thenegative electrode was referred to as a battery (A) and in the same waythe batteries using the alloy electrodes (B)-(M) were referred to asbatteries (B)-(M), respectively. Here, the capacity of the respectivebatteries was set to 650 mAh as the theoretical capacity of the nickelelectrode and a solution mixed with 7N potassium hydroxide and 1Nlithium hydroxide was used as a battery electrolyte.

Next, the respective batteries (A)-(M) were charged with 650 mA for 1.5hours and repeatedly subjected to charge/discharge cycles so that acurrent was discharged at the current of 1A until the batteries had avoltage of 1 V and the number of the cycles at which the capacity of thebatteries became 80% of an initial capacity was measured as a batterylife, and the result shown in

                  TABLE 3                                                         ______________________________________                                                     Electrode Capacity of                                                                         Battery Life                                                  Hydrogen-absorbing Alloy                                                                      (Number of                                       Specimen     (mA/g)          Cycles)                                          ______________________________________                                        Alloy Powder(A)                                                                            278             794                                              Alloy Powder(B)                                                                            251             624                                              Alloy Powder(C)                                                                            261             711                                              Alloy Powder(D)                                                                            268             750                                              Alloy Powder(E)                                                                            271             781                                              Alloy Powder(F)                                                                            268             689                                              Alloy Powder(G)                                                                            260             678                                              Alloy Powder(H)                                                                            231             426                                              Alloy Powder(I)                                                                            220             372                                              Alloy Powder(J)                                                                            251             608                                              Alloy Powder(K)                                                                            269             703                                              Alloy Powder(L)                                                                            274             776                                              Alloy Powder(M)                                                                            259             612                                              ______________________________________                                    

As apparent from the result shown in Table 3, when the alloy powderssubjected to the heat treatment are used, a high electrode capacity canbe obtained as shown in the alloy electrodes (A), (C)-(G) and (K)-(L).Further, it is confirmed that the batteries (A), (C)-(G) and (K)-(L)using the alloy powders subjected to the heat treatment can improve lifecharacteristics to 650-794 cycles.

These phenomena are assumed to be achieved by the following mechanism.That is, the heat treatment effectively acts in the alloy electrodes(A), (C)-(G) and (K)-(L) to remove fine crystal distortions in the alloystructure. As a result, a hydrogen absorbing capability per unit weightof the alloy is improved. Therefore, the electrode capacity of thesealloy electrodes is greatly increased as compared with that of the alloyelectrode (M) not subjected to the heat treatment. Further, stress isreduced when hydrogen is absorbed/released and the life characteristicsof the batteries using these alloy electrodes are greatly improved. Inparticular, it is verified that when the alloy powders (A), (D), (E),(K) and (L) subjected to the heat treatment within the temperature rangeof 250°-350° C. for 1 hour or longer are used, the effect of improvementis particularly enhanced.

On the other hand, since the alloy powder (B) is subjected to the heattreatment at the low temperature of 150° C. and the alloy powder (J) issubjected to the heat treatment for the short time of 0.5 hour, they cannot sufficiently remove the crystal distortions and can only obtainsubstantially the same electrode capacity and battery life as those ofthe alloy powder (M) not subjected to the heat treatment.

Further, since the alloy powders (H) and (I) are subjected to the heattreatment at the excessively high temperature of 550°-600° C., thecomposition of the alloy powders is varied by the reduction in theamount of the high volatile Mn and rare earth elements and the strengthof the alloys is lowered by the secondary recrystallization and thusboth the electrode capacity and battery life of them are lowered.

Embodiment 11

Various rapidly-quenched molten alloys were prepared by themolten-metal-rapidly-quenching method similar to the embodiment 10 whilechanging a substituted amount x of Mn. The rapidly-quenched moltenalloys had the composition formula of LmNi₄.3-x Co₀.4 Mn_(x) Al₀.3 andthe substituted amount of Mn was changed to 0, 0.1, 0.3, 0.5, 0.8, and1.2. Further, Lm was La-rich misch metal similar to that of theembodiment 10. The thus obtained rapidly-quenched molten alloys wereused as they are without being subjected to a heat treatment to formalloy electrodes. Further, the alloy electrodes were combined withnickel electrodes to prepare batteries and the electrode capacity andlife of the batteries were measured.

Further, the respective alloys were subjected to a heat treatment underthe conditions (heated in an Ar atmosphere at the temperature of 300° C.for 4 hours) which were most effective in the embodiment 10. Then,various hydrogen-absorbing alloy electrodes and AA type nickel-metalhydride batteries were prepared in the same way as the embodiment 10 andthe electrode capacity and battery life thereof were measured. Note, themethods of measuring electrode capacity and battery life were the sameas those of the embodiment 10.

On the other hand, as a comparative example, an electrode and batteryhaving the same specification were made by using the ingot of thehydrogen-absorbing alloy having the composition of Lm Ni₄.0 Co₀.4 Mn₀.3Al₀.3 and prepared by a melting/casing method in place of themolten-metal-rapidly-quenching method and the electrode capacity andbattery life (cycle life) thereof were measured in the same way toobtain the result shown in Table 4.

                  TABLE 4                                                         ______________________________________                                               Before Heat treatment                                                                       After Heat Treatment                                     Substituted                                                                            Electrode           Electrode                                        Amount of Mn                                                                           Capacity Cycle Life Capacity                                                                             Cycle Life                                (X)      (mAh/g)  (No. of Cycles)                                                                          (mAh/g)                                                                              (No. of Cycles)                           ______________________________________                                        0.0      221      506        228    597                                       0.1      240      541        256    693                                       0.3      259      612        278    794                                       0.5      263      557        281    762                                       0.8      268      526        283    717                                       1.2      275      410        286    475                                       Ingot(0.3)                                                                             250      412        252    406                                       ______________________________________                                    

As apparent from the result shown in Table 4, the effect of the heattreatment is small in the alloy composition not containing Mn. On theother hand, the alloy compositions containing Mn obtain a greatimprovement effect in both the electrode capacity and battery life.When, however, the substituted amount of Mn exceeds 1 and reaches 1.2,the battery life is rapidly dropped and there is no significantdifference between the characteristics of the conventional alloy ingotmade by the melting/casing method and those of the rapidly-quenchedmolten alloys.

On the other hand, since the alloy ingot made by the melting/casingmethod has the segregations caused to the components constituting thealloy ingot and located in the wide range of the crystal structurethereof, the homogeneity of the alloy is not arisen under the heattreatment conditions limited in the method of this embodiment (heated at300° C. for 4 hours). Therefore, the effect of the heat treatment is notalmost realized and thus the improvement of the battery characteristicsis difficult.

Embodiment 12

Six kinds of rapidly-quenched molten alloys were prepared by themolten-metal-rapidly-quenching method similar to the embodiment 11 whilechanging a substituted amount x of Mn. The rapidly-quenched moltenalloys had the composition of Lm Ni₄.3-x Co₀.4 Mn_(x) Cr₀.3 and thesubstituted amount of Mn was changed to 0, 0.1, 0.3, 0.5, 0.8, and 1.2.

On the other hand, as a comparative example, the ingot of ahydrogen-absorbing alloy made by the melting/casing method and havingthe composition of Lm Ni₄.0 Co₀.4 Mn₀.3 Cr₀.3 was prepared.

Then, alloy electrodes and AA type nickel-metal hydride batteries weremade by using the above various kinds of the rapidly-quenched moltenalloys and the ingot of the hydrogen-absorbing alloy in the same way asthe embodiment 11 and the electrode capacity and battery life thereofwere measured.

Further, the rapidly-quenched molten alloys and the ingot of thehydrogen-absorbing alloy were subjected to a heat treatment under theconditions (heated in an Ar atmosphere at the temperature of 300° C. for4 hours) which were most effective in the embodiment 10. Then,hydrogen-absorbing alloy electrodes and AA type nickel-metal hydridebatteries were prepared by using the various heat treated alloys and theelectrode capacity and battery life (cycle life) thereof were measuredin the same way as the embodiment 10, and the result shown in Table 5was obtained.

                  TABLE 5                                                         ______________________________________                                               Before Heat Treatment                                                                       After Heat Treatment                                     Substituted                                                                            Electrode           Electrode                                        Amount of Mn                                                                           Capacity Cycle Life Capacity                                                                             Cycle Life                                (X)      (mAh/g)  (No. of Cycles)                                                                          (mAh/g)                                                                              (No. of Cycles)                           ______________________________________                                        0.0      218      415        221    436                                       0.1      243      530        262    603                                       0.3      256      575        270    756                                       0.5      264      544        277    741                                       0.8      270      524        285    705                                       1.2      277      371        290    449                                       Ingot(0.3)                                                                             258      386        259    403                                       ______________________________________                                    

As apparent from the result shown in Table 5, the alloy composition notcontaining Mn does not almost exhibit the improvement effect of thebattery characteristics resulting from the heat treatment. On the otherhand, the electrode capacity is increased and the battery life isextended by the heat treatment in the alloy components in which thesubstituted amount x of Mn is 0.1≦x≦1.

When, however, the substituted amount x of Mn exceeds 1, it is confirmedthat the battery life is lowered to the level same as that of the casein which the ingot of cast alloy is used, in the same way as theembodiment 11.

Embodiment 13

Five kinds of rapidly-quenched molten alloys were prepared by themolten-metal-rapidly-quenching method similar to the embodiment 11 whilechanging a substituted amount x of Cu. The rapidly-quenched moltenalloys had the composition of Lm Ni₄.5-x Mn₀.5 Cu_(x) and thesubstituted amount x of Cu was changed to 0, 0.3, 0.5, 0.8, and 1.2,respectively.

On the other hand, as a comparative example, a hydrogen-absorbing alloyingot made by the melting/casting method and having the composition ofLm Ni₄.2 Mn₀.5 Cu₀.3 was prepared.

Then, alloy electrodes and AA type nickel-metal hydride batteries weremade by using the above various kinds of the rapidly-quenched moltenalloys and the ingot of the hydrogen-absorbing alloy in the same way asthe embodiment 11 and the electrode capacity and battery life thereofwere measured.

Further, the rapidly-quenched molten alloys and the ingot of thehydrogen-absorbing alloy were subjected to the heat treatment in the Aratmosphere at the temperature of 300° C. for 4 hours. Then,hydrogen-absorbing alloy electrodes and AA type nickel-metal hydridebatteries were made by using the various heat treated alloys and theelectrode capacity and battery life (cycle life) thereof were measuredin the same way as the embodiment 10, and the result shown in Table 6was obtained.

                  TABLE 6                                                         ______________________________________                                               Before Heat treatment                                                                       After Heat Treatment                                     Substituted                                                                            Electrode           Electrode                                        Amount of Cu                                                                           Capacity Cycle Life Capacity                                                                             Cycle Life                                (X)      (mAh/g)  (No. of Cycles)                                                                          (mAh/g)                                                                              (No. of Cycles)                           ______________________________________                                        0.0      270      526        283    641                                       0.3      261      548        271    673                                       0.5      249      573        260    697                                       0.8      236      563        247    671                                       1.2      207      372        214    469                                       Ingot(0.3)                                                                             253      309        256    316                                       ______________________________________                                    

In the result shown in Table 6, since the substituted amount of Mnexhibiting large meritorious effects depending upon the presence orabsence of the heat treatment is given, the variation of thecharacteristics of the alloy electrodes and batteries according to theembodiment 13 is relatively small as compared with the embodiments10-12. From the tendency as a whole, however, it can be confirmed thetendency that both the electrode capacity and battery life are increasedby the execution of the heat treatment.

Further, it is also confirmed that the electrode capacity is lowered bythe increased substituted amount of Cu and that in particular, when thesubstituted amount is 1 or more, there is a tendency that the capacityis rapidly lowered. In addition, it is also confirmed that when thesubstituted amount exceeds 1, the cycle life is rapidly shortened.

According to the hydrogen-absorbing alloys for battery of theembodiments 10-13, since the molten alloys each having the predeterminedcomposition containing Mn as an essential component element are preparedby being rapidly quenched, the alloy electrodes and batteries having aless amount of segregations, a high electrode capacity and long life canbe formed.

In particular, it is possible to remove internal distortion whilekeeping the homogeneity of the alloys by further subjecting the aboverapidly-quenched molten alloys to a heat treatment for 1 hour or longerat the temperature range of from 200° to 500° C. and preferably at thelow temperature range of from 200° to 350° C. Therefore, nickel-metalhydride batteries having more excellent battery characteristics can beprovided.

Embodiments 1A-9A

Hydrogen-absorbing alloy electrodes according to embodiments 1A-9A wereprepared, respectively under the same conditions as those of theembodiments 1-9 except that hydrogen-absorbing alloys were made in sucha manner that the respective rapidly-quenched molten alloys prepared bythe single roll method in the embodiments 1-9 were further subjected toa heat treatment in an Ar gas atmosphere at the temperature of 300° C.for 4 hours. Further, the respective hydrogen-absorbing alloy electrodes(negative electrodes) were combined with a nickel electrode (positiveelectrode) to make AA type nickel-metal hydride batteries.

Next, the area ratios of the columnar structures, minor diameters of thecolumnar structures, maximum electrode capacity, life (the number ofcharge-discharge cycles), and the rising-up of the initial batterycharacteristics of the hydrogen-absorbing alloys were measured under thesame conditions as those of the embodiment 1 and the like, and theresults shown in Table 7 was obtained.

                                      TABLE 7                                     __________________________________________________________________________                                                      Characteristics                                      Area Ratio of Columnar Structures                                                                 Minor         Number                                  RPM of                                                                            Aspect Ratio        Dia of        of                                 Manu-                                                                              Cooling                                                                           1:2 1:3 1:4 1:5     Columnar                                                                           Electrode                                                                          Cycle                                                                             Acti-              Specimen        facturing                                                                          Roll                                                                              or  or  or  or  As a                                                                              Structures                                                                         Capacity                                                                           Life                                                                              vation             No.  Alloy Composition                                                                        Method                                                                             (r.p.m)                                                                           higher                                                                            higher                                                                            higher                                                                            higher                                                                            whole                                                                             (μm)                                                                            (mAh/g)                                                                            (cycles)                                                                          (times)            __________________________________________________________________________    Embodi-                                                                            LmNi.sub.4.0 Co.sub.0.4 Mn.sub.0.3 Al.sub.0.3                                            Single                                                                             600 95  89  82  75  63  2.5  278  794 3                  ment 1A         Roll                                                                          Method                                                        Embodi-                                                                            LmNi.sub.3.6 Co.sub.0.4 Mn.sub.0.5 Al.sub.0.3                                            Single                                                                             600 93  87  80  72  62  2.3  281  762 2                  ment 2A         Roll                                                                          Method                                                        Embodi-                                                                            LmNi.sub.4.0 Co.sub.0.4 Mn.sub.0.3 Cr.sub.0.3                                            Single                                                                             600 97  85  79  71  60  2.3  270  756 3                  ment 3A         Roll                                                                          Method                                                        Embodi-                                                                            LmNi.sub.3.6 Co.sub.0.4 Mn.sub.0.5 Cr.sub.0.5                                            Single                                                                             600 96  92  86  81  78  2.3  277  741 2                  ment 4A         Roll                                                                          Method                                                        Embodi-                                                                            LmNi.sub.4.2 Mn.sub.0.5 Cu.sub.0.8                                                       Single                                                                             600 98  93  87  78  62  2.6  271  673 2                  ment 5A         Roll                                                                          Method                                                        Embodi-                                                                            LmNi.sub.4.2 Mn.sub.0.8                                                                  Single                                                                             600 94  90  82  79  65  2.7  283  548 1                  ment 6A         Roll                                                                          Method                                                        Embodi-                                                                            LmNi.sub.4.4 Mn.sub.0.3 Al.sub.0.3                                                       Single                                                                             600 97  89  77  73  45  2.5  274  567 2                  ment 7A         Roll                                                                          Method                                                        Embodi-                                                                            LmNi.sub.4.0 Co.sub.0.4 Mn.sub.0.3 Fe.sub.0.3                                            Single                                                                             600 96  91  89  79  68  2.4  262  589 2                  ment 8A         Roll                                                                          Method                                                        Embodi-                                                                            LmNi.sub.4.0 Co.sub.0.4 Mn.sub.0.3 Si.sub.0.3                                            Single                                                                             600 93  90  86  77  67  2.2  256  562 2                  ment 9A         Roll                                                                          Method                                                        __________________________________________________________________________

As apparent from the result shown in Table 7, since thehydrogen-absorbing alloys of the respective embodiments having beensubjected to the heat treatment at the relatively low temperature of300° C. effectively correct crystal distortions without damaging thehomogeneity thereof, hydrogen can be easily absorbed and disabsorbed.Therefore, it is verified that the electrode capacity and the cycle lifeof the batteries are greatly improved as compared with the batteriesusing the respective hydrogen-absorbing alloys shown in Table 1. Inparticular, the battery capacity is increased by about 10%.

Comparative Examples 1A-1D

Molten alloys were rapidly quenched by using a double roll apparatushaving two iron cooling rolls with a diameter of 100 mm disposed inconfrontation to each other as shown in FIG. 2 and hydrogen-absorbingalloys according to comparative examples 1A-1D having the finalcomposition of Mm Ni₃.55 Mn₀.4 Al₀.3 Co₀.75 were prepared. Note, therotation speed of the cooling rolls was set to 1500 rpm (comparativeexample 1A), 2000 rpm (comparative example 1B), 2500 rpm (comparativeexample 1C) and 3000 rpm (comparative example 1D), respectively.

Comparative Examples 2A-2D, 3A and 3B

Molten alloys were rapidly quenched by using a single roll apparatushaving a copper cooling roll with a diameter of 300 mm andhydrogen-absorbing alloys according to comparative examples 2A-2D and3A-3B having the final compositions shown in Table 8 were prepared.Note, the rotation speed of the cooling roll was set to 1000 rpm(comparative example 2A), 1500 rpm (comparative example 2B), 2000 rpm(comparative examples 2B' and 2C), 2500 rpm (comparative example 2D),200 rpm (comparative example 3A), and 200 rpm (comparative example 3B),respectively. Note, the rapid quenching was carried out in an Ar gasatmosphere at 1 atm., the distance between the extreme end of aninjection nozzle for injecting the molten alloys and the cooling rollwas set to 50 mm, and an injection pressure was set to 0.1 Kgf/cm².

Comparative Examples 4-6

Molten alloys were rapidly quenched by using a single roll apparatushaving a copper cooling roll with a diameter of 300 mm andhydrogen-absorbing alloys according to comparative examples 4-6 havingthe final compositions shown in Table 8 were prepared, respectively.Note, the rapid quenching was carried out in an Ar gas atmosphere at 1atm., the distance between the extreme end of an injection nozzle forinjecting the molten alloys and the cooling roll was set to 50 mm, aninjection pressure was set to 0.02 Kgf/cm², and the rotation speed ofthe cooling roll was set to 1000 rpm.

Note, as crucibles for preparing the molten alloys, there were used acrucible made of calcia (comparative example 4), a crucible made ofalumina (comparative example 5) and a crucible made of quartz(comparative example 6), respectively.

Comparative Examples 7A-7D

A Molten alloy was rapidly quenched by using a single roll apparatushaving a ceramic spray coated roll having a diameter of 300 mm andhydrogen-absorbing alloys according to comparative examples 7A-7D havingthe final compositions of Lm Ni₄.2 Co₀.2 Mn₀.3 Al₀.3 were prepared.Note, the rapid quenching was carried out in an Ar gas atmosphere at 1atm., the distance between the extreme end of an injection nozzle forinjecting the molten alloy and the ceramic spray coating roll was set to50 mm, an injection pressure was set to 0.1 Kgf/cm². Further, therotation speed of the ceramic spray coating roll was set to 1000 rpm(comparative example 7A), 1500 rpm (comparative example 7B), 2000 rpm(comparative examples 7C), and 2500 rpm (comparative example 7D),respectively.

Comparative Examples 8A-9B

Molten alloys were rapidly quenched by using a single roll apparatushaving a copper cooling roll with a diameter of 200 mm andhydrogen-absorbing alloys according to comparative examples 8A-9B havingthe final compositions shown in Table 9 were prepared. Note, the rapidquenching was carried out in an Ar gas atmosphere at 1 atm., thedistance between the extreme end of an injection nozzle for injectingthe molten alloys and the cooling roll was set to 50 mm, an injectionpressure was set to 100 mm-H₂ O, and the rotation speed of the coolingroll was set to 2000 rpm (comparative examples 8A), 2500 rpm(comparative example 8B), 2000 rpm (comparative examples 9A), and 2500rpm (comparative example 9B), respectively.

Comparative Examples 10-13

The materials of hydrogen-absorbing alloy powder were adjusted so thatthe compositions of alloy ingots had the composition of Mm Ni₃.2 Co₁.4Al₀.6 (comparative example 10), Mm Ni₃.2 Co₁.1 Al₀.7 (comparativeexample 11), Mm Ni₃.5 Co₀.7 Al₀.8 (comparative example 12), and Mn Ni₃.7Co₀.4 Al₀.9 (comparative example 13), respectively and were put into acrucible made of alumina, and molten alloys were prepared by meltingthem at 1400° C. by a high frequency induction heating. Next, the moltenalloys were cast in a water-cooled steel casting mold and solidified tomake the ingots of the hydrogen-absorbing alloys according to thecomparative examples 10-13, respectively.

Comparative Examples 14A-14B

The material of a hydrogen-absorbing alloy powder adjusted so that thecomposition of an alloy ingot had the composition of Ni₃.55 Co₀.75 Mn₀.4Al₀.3 was put into a crucible made of mullite and melted by being heatedto 1500° C. by a high frequency induction heating coil disposed aroundthe outside periphery of the crucible to prepare a molten alloy. Next,the thus obtained molten alloy was cast in a water-cooled steel castingmold and alloy ingots were prepared with the distance between castingmold surfaces set to 55 mm (comparative example 14A) and 35 mm(comparative example 14B) at a casting speed of 3 Kg/sec./m². Further,the thus obtained alloy ingots were subjected to a heat treatment in anargon gas atmosphere at 1050° C. for 6 hours to preparehydrogen-absorbing alloys according to the comparative examples 14A-14B,respectively.

Comparative Examples 15-20

As comparative examples 15, 16, 18-20, the materials ofhydrogen-absorbing alloy powders adjusted so that the composition ofalloy ingots had the values shown in Table 9 were put into a cruciblemade of alumina and heated to 1400° C. by high frequency inductionheating to prepare molten alloys. Note, in the comparative example 17,the molten alloy was prepared by an arc melting method. Next, the thusobtained respective molten alloys were cast in a water-cooled castingmold and solidified to prepare the ingots of hydrogen-absorbing alloysaccording to the comparative examples 15-20. In addition, the ingot ofthe hydrogen-absorbing alloy of the comparative example 16 was furthersubjected to a heat treatment in an Ar gas atmosphere at 1000° C. for 6hours.

The thus obtained rapidly-quenched molten alloys or hydrogen-absorbingalloys according to the comparative examples 1A-20 were pulverized by astamp mill and classified to 200 mesh or less to preparehydrogen-absorbing alloy powders for battery. Next, hydrogen-absorbingalloy electrodes (negative electrodes) were prepared by using therespective hydrogen-absorbing alloy powders for battery in the sameprocedure as that of the embodiment 1 and combined with a nickelelectrode (positive electrode) to assemble AA type nickel-metal hydridebatteries. Then, the electrode capacity, the number of charge/dischargecycles (life) and the number of activations of the electrodes weremeasured by the same method as that of the embodiment 1 and the resultsshown in Tables 8 and 9 were obtained.

                                      TABLE 8                                     __________________________________________________________________________                                         Area Ratio of Columnar Structures                                             (%)                                                                       RPM of                                                                            Aspect Ratio                                                              Cooling                                                                           1:2 1:3 1:4 1:5                                                  Manufacturing                                                                          Roll                                                                              or  or  or  or  As a                     Specimen No.                                                                              Alloy Composition                                                                         Method   (r.p.m)                                                                           higher                                                                            higher                                                                            higher                                                                            higher                                                                            whole                    __________________________________________________________________________    Comparative Example 1A                                                                    MmNi.sub.3.55 Mn.sub.0.3 Al.sub.0.3 Co.sub.0.75                                           Single Roll Method                                                                     1500                                                                              48  44  35  25  22                       Comparative Example 1B                                                                    MmNi.sub.3.55 Mn.sub.0.4 Al.sub.0.3 Co.sub.0.75                                           Single Roll Method                                                                     2000                                                                              38  30  25  15  19                       Comparative Example 1C                                                                    MmNi.sub.3.55 Mn.sub.0.4 Al.sub.0.3 Co.sub.0.75                                           Single Roll Method                                                                     2500                                                                              33  28  20  12  12                       Comparative Example 1D                                                                    MmNi.sub.3.55 Mn.sub.0.4 Al.sub.0.3 Co.sub.0.75                                           Single Roll Method                                                                     3000                                                                              25  19  13   7  10                       Comparative Example 2A                                                                    MmNi.sub.3.3 CoAl.sub.0.3 Mn.sub.0.5                                                      Single Roll Method                                                                     1000                                                                              49  47  38  31  23                       Comparative Example 2B                                                                    MmNi.sub.3.2 CoAl.sub.0.2 Mn.sub.0.5                                                      Single Roll Method                                                                     1500                                                                              40  33  22  17  19                       Comparative Example 2B*                                                                   Mm.sub.1.4 Ni.sub.3.2 CoAl.sub.0.2 Mn.sub.0.5                                             Single Roll Method                                                                     2000                                                                              25  18  15   9   8                       Comparative Example 2C                                                                    MmNi.sub.3.2 CoAl.sub.0.2 Mn.sub.0.5                                                      Single Roll Method                                                                     2000                                                                              21  18  10   7   8                       Comparative Example 2D                                                                    MmNi.sub.3.2 CoAl.sub.0.2 Mn.sub.0.5                                                      Single Roll Method                                                                     2500                                                                               9   8   5   2   3                       Comparative Example 3A                                                                    MmNi.sub.3.2 CoAl.sub.0.2 Mn.sub.0.5                                                      Single Roll Method                                                                      200                                                                              11  10   8   5   3                       Comparative Example 3B                                                                    Mm.sub.1.4 Ni.sub.3.2 CoAl.sub.0.2 Mn.sub.0.5                                             Single Roll Method                                                                      200                                                                              10   9   7   4   2                       Comparative Example 4                                                                     MmNi.sub.5 Ca.sub.0.01                                                                    Single Roll Method                                                                     1000                                                                              13  12   9   5   6                       Comparative Example 5                                                                     MmNi.sub.5 Al.sub.0.01                                                                    Single Roll Method                                                                     1000                                                                              10   9   5   2   4                       Comparative Example 6                                                                     MmNi.sub.5 Si.sub.0.01                                                                    Single Roll Method                                                                     1000                                                                              15   9   7   3   7                       Comparative Example 7A                                                                    LmNi.sub.4.2 Co.sub.0.2 Mn.sub.0.3 Al.sub.0.3                                             Single Roll Method                                                                     1000                                                                              47  41  35  19  21                       Comparative Example 7B                                                                    LmNi.sub.4.2 Co.sub.0.2 Mn.sub.0.3 Al.sub.0.3                                             Single Roll Method                                                                     1500                                                                              31  28  21  19  12                       Comparative Example 7C                                                                    LmNi.sub.4.2 Co.sub.0.2 Mn.sub.0.3 Al.sub.0.3                                             Single Roll Method                                                                     2000                                                                              15  14   8   5   8                       Comparative Example 7D                                                                    LmNi.sub.4.2 Co.sub.0.2 Mn.sub.0.3 Al.sub.0.3                                             Single Roll Method                                                                     2500                                                                               7   6   4   2   2                       __________________________________________________________________________                                         Minor Dia of                                                                        Characteristics                                                         Columnar                                                                            Electrode                                                                          Cycle                                                                             Number of                                                      Structures                                                                          Capacity                                                                           Life                                                                              Activation                                         Specimen No.                                                                              (μm)                                                                             (mAh/g)                                                                            (cycles)                                                                          (times)                   __________________________________________________________________________                             Comparative Example 1A                                                                    2.2   212  521 7                                                  Comparative Example 1B                                                                    2.1   208  501 6                                                  Comparative Example 1C                                                                    2.2   210  485 6                                                  Comparative Example 1D                                                                    1.8   212  468 6                                                  Comparative Example 2A                                                                    2.2   228  515 7                                                  Comparative Example 2B                                                                    2.0   227  497 8                                                  Comparative Example 2B*                                                                   1.8   235  415 7                                                  Comparative Example 2C                                                                    1.9   229  473 6                                                  Comparative Example 2D                                                                    1.6   226  456 7                                                  Comparative Example 3A                                                                    2.3   223  459 8                                                  Comparative Example 3B                                                                    2.0   235  430 7                                                  Comparative Example 4                                                                     1.6   204  317 7                                                  Comparative Example 5                                                                     1.8   208  342                                                    Comparative Example 6                                                                     1.7   199  357 7                                                  Comparative Example 7A                                                                    2.4   227  480 5                                                  Comparative Example 7B                                                                    1.8   223  467 7                                                  Comparative Example 7C                                                                    1.7   225  465 6                                                  Comparative Example 7D                                                                    1.7   226  448 6                         __________________________________________________________________________

                                      TABLE 9                                     __________________________________________________________________________                                         Area Ratio of Columnar Structures                                             (%)                 Minor                                                 RPM of                                                                            Aspect Ratio        Dia of                                                Cooling                                                                           1:2 1:3 1:4 1:5     Columnar                                     Manufacturing                                                                          Roll                                                                              or  or  or  or  As                                                                                Structures           Specimen No.                                                                              Alloy Composition                                                                         Method   (r.p.m)                                                                           higher                                                                            higher                                                                            higher                                                                            higher                                                                            whole                                                                             (μm)              __________________________________________________________________________    Comparative Example 8A                                                                    LaNi.sub.4.6 Al.sub.0.4                                                                   Single Roll Method                                                                     2000                                                                              12  11  7   5   3   2.4                  Comparative Example 8B                                                                    LaNi.sub.4.6 Al.sub.0.4                                                                   Single Roll Method                                                                     2500                                                                               6   5   3   1>  2  2.2                  Comparative Example 9A                                                                    LaNi.sub.4.0 Co.sub.0.5 Al.sub.0.4                                                        Single Roll Method                                                                     2000                                                                              21  18  13   7   9  2.1                  Comparative Example 9B                                                                    LaNi.sub.4.0 Co.sub.0.5 Al.sub.0.4                                                        Single Roll Method                                                                     2500                                                                               9   4   2   1> 3   2.2                  Comparative Example 10                                                                    MmNi.sub.3.0 Co.sub.1.4 Al.sub.0.6                                                        Casting Method                                                                         --  30  28  25  22  14  2.6                  Comparative Example 11                                                                    MmNi.sub.3.2 Co.sub.1.1 Al.sub.0.7                                                        Casting Method                                                                         --  39  37  31  23  23  2.5                  Comparative Example 12                                                                    MmNi.sub.3.7 Co.sub.0.4 Al.sub.0.9                                                        Casting Method                                                                         --  35  31  29  25  16  2.2                  Comparative Example 13                                                                    MmNi.sub.3.7 Co.sub.0.4 Al.sub.0.9                                                        Casting Method                                                                         --  28  23  17  11  13  2.5                  Comparative Example 14A                                                                   MmNi.sub.3.55 Co.sub.0.75 Mn.sub.0.4 Al.sub.0.3                                           Casting Method                                                                         --  85  43  22  10   5  120                  Comparative Example 14B                                                                   MmNi.sub.3.55 Co.sub.0.75 Mn.sub.0.4 Al.sub.0.3                                           Casting Method                                                                         --  93  47  35  27  11  100                  Comparative Example 15                                                                    MmNi.sub.3.5 Co.sub.0.7 Al.sub.0.5                                                        Casting Method                                                                         --  Max. Crystal Grain Size 150 μm        Comparative Example 16                                                                    MmNi.sub.3.7 Al.sub.0.5 Fe.sub.0.7 Cu.sub.0.1                                             Casting Method                                                                         --  Max. Crystal Grain Size 200 μm        Comparative Example 17                                                                    MmNi.sub.3.8 Co.sub.0.2 Al.sub.0.5                                                        Casting Method                                                                         --  Max. Crystal Grain Size 100 μm        Comparative Example 18                                                                    LaNi.sub.4.5 Al.sub.0.5                                                                   Casting Method                                                                         --  Max. Crystal Grain Size 170 μm        Comparative Example 19                                                                    LaNi.sub.4.7 Al.sub.0.3                                                                   Casting Method                                                                         --  Max. Crystal Grain Size 180 μm        Comparative Example 20                                                                    LaNi.sub.4.2 Co.sub.0.3 Sn.sub.0.2 Al.sub.0.3                                             Casting Method                                                                         --  Max. Crystal Grain Size 170              __________________________________________________________________________                                         μm                                                                                     Characteristics                                                               Electrode                                                                          Cycle                                                                             Number of                                                            Capacity                                                                           Life                                                                              Activation                                                           (mAh/g)                                                                            (cycles)                                                                          (times)             __________________________________________________________________________                                         Comparative Example                                                                       225  376 6                                                        Comparative Example                                                                       223  360 7                                                        Comparative Example                                                                       200  462 6                                                        Comparative Example                                                                       205  447 7                                                        Comparative Example                                                                       200  497 8                                                        Comparative Example                                                                       207  525 8                                                        Comparative Example                                                                       215  509 7                                                        Comparative Example                                                                       219  475 8                                                        Comparative Example                                                                       260  432 6                                                        Comparative Example                                                                       262  441 7                                                        Comparative Example                                                                       200  520 9                                                        Comparative Example                                                                       210   70 8                                                        Comparative Example                                                                       208  440 7                                                        Comparative Example                                                                       220  385 7                                                        Comparative Example                                                                       233  370 5                                                        Comparative Example                                                                       207  390 6                   __________________________________________________________________________

As apparent from the result shown in Table 8 and Table 9, in each of thehydrogen-absorbing alloys shown in the comparative examples 1A-20, thearea ratio of the columnar structures in a metal structure is reduced ascompared with that of the embodiments shown in Tables 1 and 7.Therefore, it is confirmed that the electrode capacity using thesealloys is low and the battery life (cycle life) represented by thenumber of charge/discharge cycles is also short.

Further, in the electrodes of the comparative examples, the number ofcharge/discharge cycles (the number of activations) necessary to obtaina maximum electrode capacity is 5-9 times which are twice or more the2-3 times of the embodiments, and thus it is confirmed that the initialrising-up property of the electrodes is also low.

In particular, the columnar structures are not sufficiently grown evenin the hydrogen-absorbing alloys according to the comparative examples1A-1D, 2A-2D, 3A-3B, 7A-7D each added with Mn in the same way as theembodiments and the ratio of equi-axed crystals are increased in somecases, and thus the battery characteristics are lowered as compared withthe embodiments shown in Tables 1 and 7.

FIG. 27 is a photograph taken by an electron microscope (SEM) to showthe metal structure of the cross section of the hydrogen-absorbing alloyaccording to the comparative example 7B. In FIG. 27, the lower portionof the cross section is a quenched side in contact with the cooling rolland the upper portion thereof is a free side. Columnar structures aregrown from the quenched side toward the free side, whereas an equi-axedcrystal structure is formed in the portion near to the free side becauseof an insufficient quenching rate. The area ratio of the columnarstructures in an entire crystal structure is 50% or less.

Further, in the batteries using the hydrogen-absorbing alloys accordingto the comparative examples 4, 5, 6 8A-9B to which Mn is not contained,an electrode capacity is about 200-225 mAh/g and further a battery lifeis as low as 300-400 cycles.

Further, it is found that the hydrogen-absorbing alloys according to thecomparative examples 10-13 made by being gradually cooled by the castingmethod have a small area ratio of columnar structures, low electrodecapacity and a bad initial rising-up property of electrode.

On the other hand, it is found that the hydrogen-absorbing alloyscontaining Mn according to the comparative examples 14A-14B made bybeing gradually cooled by the casting method have sufficiently growncolumnar structures, but a battery life is short and an initialrising-up property of electrode is bad because the minor diameter of thecolumnar structures is as large as 100-120 microns, although arelatively high electrode capacity can be obtained.

Further, the hydrogen-absorbing alloys without containing Mn accordingto the comparative examples 15-20 made by being gradually cooled by thecasting method have a crystal particle size increased to about 100-200microns, and thus an alloy strength is lowered and a battery life isshort.

As described above, when the respective embodiments shown in Tables 1and 7 are compared with the respective comparative examples shown inTables 8 and 9, it is found that the hydrogen-absorbing alloys andbatteries according to the embodiments satisfy all of the three leadingcharacteristics of the electrode capacity, battery life and initialrising-up property.

Next, the relationship between the crystal particle size and the batterylife of hydrogen-absorbing alloy will be described with reference to thefollowing embodiments and comparative examples.

Embodiments 14-17 and Comparative Examples 21-22

The material of an alloy powder adjusted so that the composition of ahydrogen-absorbing alloy was Lm Ni₄.0 Co₀.4 Mn₀.3 Al₀.3 was put into aan crucible and heated by high frequency induction heating to prepare amolten alloy.

As embodiments 14-17, respective hydrogen-absorbing alloys were made byrapidly quenching the molten alloy by using a single roll apparatushaving a cooling roll with a diameter of 300 mm. The material and therotating speed of the cooling roll were set as shown in Table 10.

On the other hand, as comparative examples 21-22, respectivehydrogen-absorbing alloys were made in such a manner that the abovemolten alloy was put into a water-cooled copper casting mold and castwith the distance between casting mold surfaces set to 45 mm(comparative example 21) and 80 mm (comparative example 22).

Hydrogen-absorbing alloy electrodes (negative electrodes) were preparedby crushing the hydrogen-absorbing alloys according to the embodiments14-17 and comparative examples 21-22 under the same conditions as thoseof the embodiment 1 and further combined with nickel electrodes(positive electrodes) to prepare nickel-metal hydride batteries. Then,the number of charge/discharge cycles of the respective batteries wasmeasured under the same conditions as the embodiment 1, and the resultshown in Table 10 was obtained.

                                      TABLE 10                                    __________________________________________________________________________                                   Dia. of Crystal                                                 Material of                                                                           RPM of                                                                              Grains Cycle                                           Manufacturing                                                                          Cooling Roll or                                                                       Cooling Roll                                                                        (Minor Dia.)                                                                         Life                                    Specimen No.                                                                          Method   Casting Mold                                                                          (r.p.m.)                                                                            (μm)                                                                              (cycles)                                __________________________________________________________________________    Embodiment 14                                                                         Single Roll Method                                                                     Cu      600   2.5    612                                     Embodiment 15                                                                         Single Roll Method                                                                     Fe      600   9      593                                     Embodiment 16                                                                         Single Roll Method                                                                     Fe + 5 μm thick                                                                    600   19     543                                                      Cr plated                                                    Embodiment 17                                                                         Single Roll Method                                                                     Si.sub.3 N.sub.4                                                                      300   28     511                                     Comparative                                                                           Casting Method                                                                         Cu      --    83     448                                     Example 21                                                                    Comparative                                                                           Casting Method                                                                         Cu      --    105    440                                     Example 22                                                                    __________________________________________________________________________

Further, FIG. 28 shows the relationship between the crystal particlesize and the cycle life. Note, in the embodiments 14-17 having growncolumnar structures, the crystal particle size is shown by a minordiameter.

As apparent from the result shown in Table 10 and FIG. 28, it is foundthat as the crystal particle size is increased, a battery life tends tobe rapidly shortened. To achieve the battery life (the number ofcharge/discharge cycles) of 500 cycles or more, the crystal particlesize of the hydrogen-absorbing alloy used to negative electrode must beset to 30 microns or less.

Embodiments 18A-18C and Comparative Example 23

As embodiments 18A-18C, the material of an alloy powder adjusted so thatthe composition of a hydrogen-absorbing alloy was Lm Ni₀.4 Co₀.4 Mn₀.3Al₀.3 was put into a crucible made of Ti-boride and heated by highfrequency induction heating to prepare a molten alloy. On the otherhand, the molten alloy was rapidly quenched at an average quenching rateof 2400°-3100° C./sec. by using a single roll apparatus having a coolingroll (cooling water temperature: 20° C.) with a diameter of 300 mm madeof copper to make the hydrogen-absorbing alloys of the embodiments18A-18C.

The quenching rate was calculated as follows. When the molten alloy wasinjected from an nozzle, the molten alloy was rapidly quenched andsolidified because the heat thereof was conducted to the cooling roll,and then the rapidly quenched and solidified alloy was exfoliated fromthe cooling roll and driven away from the cooling roll: when the coolingroll was rotated at about 600 rpm, the rapidly quenched alloy wasexfoliated and driven away from the cooling roll after it had beencompletely solidified, whereas when the cooling roll was rotated atabout 1000 rpm, the rapidly quenched alloy was exfoliated and drivenaway from the cooling roll before it had been completely solidifiedbecause the cooling roll had a strong centrifugal force. Although themoving distance of the molten alloy from the time at which it came intocontact with the cooling roll to the time at which it was exfoliatedtherefrom changed depending upon the composition of the alloy, when theinjecting state of the molten metal of the embodiment 18A (rotation: 600rpm) was photographed by a high-speed video camera, that distancecorresponded to 1/8 rotation of the cooling roll. When the timenecessary to move this distance was assumed to be a quenching time, thequenching time was 1/80 sec. Then, since the time necessary to drop thetemperature of the molten alloy from an injecting temperature (1380° C.)to a solidifying point (1350° C.) was 1/80 sec., the quenching rate wasabout 2400° C./sec. Since, however, there was a dispersion in theposition where the alloy was exfoliated, an average quenching rate wasemployed.

On the other hand, as a comparative example 23, the material of an alloypowder adjusted so that the composition of a hydrogen-absorbing alloywas Lm Ni₃.5 Co₀.7 Mn₀.4 Zn₀.1 Al₀.3 was put into a crucible made ofalumina and heated by high frequency induction heating to prepare amolten alloy. On the other hand, the molten alloy was rapidly quenchedat a quenching rate of 1150° C./sec. by using a single roll apparatushaving an iron cooling roll (cooling water temperature: 50° C., rpm:200) with a diameter of 300 mm to make the hydrogen-absorbing alloy.

Then, hydrogen-absorbing alloy electrodes (negative electrodes) wereprepared by crushing the hydrogen-absorbing alloys according to theembodiments 18A-18C and comparative example 23 under the same conditionsas those of the embodiment 1 and further combined with nickel electrodes(positive electrodes) to prepare nickel-metal hydride batteries. Then,the number of charge/discharge cycles of the respective batteries wasmeasured under the same conditions as the embodiment 1 as well as thehydrogen-absorbing alloys were taken out and the ratio of the columnarstructures in the metal structure of each of the hydrogen-absorbingalloys was measured, and the result shown in Table 11 was obtained.

                                      TABLE 11                                    __________________________________________________________________________                 Area Ratio of            Characteristics                                      Columnar Structures (%)                                                                           Minor     No. of                                     Average                                                                            Aspect Ratio        Dia of    Charge/                                    Quenching                                                                          1:2 1:3 1:4 1:5     Columnar                                                                           Electrode                                                                          Discharge                                                                          No. of                                Rate or  or  or  or  As a                                                                              Structures                                                                         Capacity                                                                           Cycles                                                                             Activation                    Specimen No.                                                                          (°C./sec)                                                                   higher                                                                            higher                                                                            higher                                                                            higher                                                                            Whole                                                                             (μm)                                                                            (mAh/g)                                                                            (cycles)                                                                           (times)                       __________________________________________________________________________    Embodiment 18A                                                                        2400 96  90  83  75  63  1.9  261  610  3                             Embodiment 18B                                                                        2700 94  91  87  77  65  1.7  263  612  2                             Embodiment 18C                                                                        3100 95  93  84  78  63  1.7  262  612  2                             Comparative                                                                           1150 20  18   9   7  2.2 5    255  480  4                             Example 23                                                                    __________________________________________________________________________

As apparent from the result shown in Table 11, the alloys according tothe embodiments 18A-18C prepared at the increased peripheral speed ofthe cooling roll and the high quenching rate have sufficiently growncolumnar structures and exhibit excellent battery characteristics ascompared with the comparative example 23 quenched at the low quenchingrate.

Embodiment 19

Next, the composition ratio x of a rare earth element A and the otherelements B in the hydrogen-absorbing alloy composed AB_(x) was changedin the range of from 4.4 to 6.1 and the effect of the change of thecomposition ratio x on the electrode capacity and the number ofcharge/discharge cycles was investigated. That is, varioushydrogen-absorbing alloys represented by Lm (Ni₀.8 Co₀.08 Mn₀.06Al₀.06)_(x) were made by rapidly quenching a molten alloy at a quenchingrate of 2400° C./sec.

When the composition ratio x=5, this hydrogen-absorbing alloycorresponded to the hydrogen-absorbing alloy of the first embodiment.The thus obtained respective hydrogen-absorbing alloy were processed inthe same way as the embodiment 1 to make negative electrodes, and theelectrode capacity of the negative electrodes was measured as well asthe negative electrodes were combined with a positive electrode toassemble nickel-metal hydride batteries and the number ofcharge/discharge cycles thereof were measured, and the result shown inFIG. 31 was obtained.

As apparent from the result shown in FIG. 31, it is confirmed that theelectrode capacity is 240 mAh/g or more within the range of 4.5≦x≦6.0limited in the present invention and the excellent batterycharacteristics such as the number of charge/discharge cycles of 500times or more are achieved. Further, it is also verified that theexcellent battery characteristics of the electrode capacity of 250 mAh/gor more and the number of charge/discharge cycles of 550 times or moreare achieved in the more preferable range (4.6≦x≦5.8) of the compositionratio x.

As described above, the hydrogen-absorbing alloy for battery accordingto this embodiment is an AB₅ type alloy containing Mn as an essentialelement, which can provide a negative electrode material having a highelectrode capacity and excellent cycle life and initial characteristicsused to secondary nickel-metal hydride battery because the componentsconstituting the hydrogen-absorbing alloy have a less amount ofsegregations. The above alloy can be obtained by rapidly quenching amolten alloy at a quenching rate of 1800° C./sec. or higher.

Further, internal distortions can be removed while maintaining thehomogeneity of the alloy by subjecting the above rapidly-quenched moltenalloy to a heat treatment at a relatively low temperature of about200°-500° C., by which a nickel-metal hydride battery excellent inbattery characteristics can be provided.

Further, other embodiments of the present invention will be describedtogether with comparative examples.

Embodiment 20

(Manufacture of Alloy)

When a hydrogen-absorbing alloy having a stoichiometric composition ofLmNi₄.0 Co₀.4 Mn₀.3 Al₀.3 (Lm: La-rich misch metal) was made, materialswere weighed in the weight ratio for achieving a non-stoichiometriccomposition without destroying the composition ratio of Ni, Co, Mn, Alby reducing the amount of Lm when the materials were weighed. Next,these materials were melted in a high frequency induction heatingfurnace and accommodated to the ladle 2 of the aforesaid manufacturingapparatus employing the single roll method shown in FIG. 1 and a moltenhydrogen-absorbing alloy 3 was dropped onto a cooled cooling roll 5 fromthe ladle 2 so that six kinds of flake-shaped hydrogen-absorbing alloys6 (specimens a-f) were obtained.

The composition of the thus obtained alloys is shown in Table 12.Further, these alloys were pulverized in a ball mill and then classifiedthrough a sieve of 200 mesh to make hydrogen-absorbing alloys forelectrode.

                  TABLE 12                                                        ______________________________________                                                         Alloy Composition                                            Symbol of Alloy Specimen                                                                       (AB.sub.x)                                                   ______________________________________                                        a                AB.sub.5.0                                                   b                .sub. AB.sub.5.05                                            c                AB.sub.5.5                                                   d                AB.sub.5.8                                                   e                AB.sub.6.0                                                   f                AB.sub.6.2                                                   ______________________________________                                    

Further, the thus obtained hydrogen-absorbing alloys (specimens a-f inTable 12) were measured by an X-ray diffraction in accordance with aninternal standard method. As a result, it is confirmed that 95 vol % ormore of the specimens a-e was a single phase composed of AB_(x).Further, it is also found that 10 vol % or more of a phase (secondphase) having a composition other than AB_(x) is grown in the specimenf.

(Manufacture of Electrode)

The respective hydrogen-absorbing alloy powders, polytetrafluoroethylene(PTFE) powder and ketchen black were weighed to 95.5 wt %, 4 wt % and0.5 wt %, respectively and then stirred and mixed by a cutter mill untilthe PTFE was made to fibers. The thus obtained cotton-like mixture wasscattered onto a nickel metal net and rolled by a roller press to makehydrogen-absorbing alloy electrodes (negative electrodes).

(Manufacture of Battery)

A paste was prepared by adding a small amount of CMC (carboxymethylcellulose) and 50 wt % of water to 90 wt % of nickel hydroxide and 10 wt% of cobalt monoxide and stirring and mixing them. That paste was filledto a porous nickel member having a three-dimensional structure and driedand rolled by a roller press to make nickel electrodes (positiveelectrodes).

Groups of electrodes were arranged in such a manner that each of theabove nickel electrodes having a theoretical capacity of 1.1 Ah wascombined with each of the above hydrogen-absorbing alloy electrodes andthey were wound through a separator composed of a non-woven fabric. Thegroups of the electrodes were inserted into AA type battery cans(containers), and each of the cans was filled with 30 wt % potassiumhydroxide aqueous solution and sealed by the terminal plate of apositive electrode having a safety valve operating at a pressure of 15Kg/cm² to assemble secondary nickel-metal hydride batteries shown inFIG. 3. Note, in the secondary nickel-metal hydride battery, a negativeelectrode/positive electrode ratio was set to 1.8 and the amount ofbattery electrolyte to the hydrogen-absorbing alloy electrode was set to1.1 ml/Ah. The negative electrode/positive electrode ratio means thecapacity ratio of the alloy in an uncharged state in the batterydischarged state of the hydrogen-absorbing alloy electrode. That is,this means the ratio of the capacity of the hydrogen-absorbing alloyelectrode to that of the nickel electrode, excluding the dischargereserve in the hydrogen-absorbing alloy electrode produced by theoxidation and the like of the cobalt monoxide in the nickel electrodewhen the battery is charged for the first time after has been assembled.

The cycle life of the respective secondary batteries was evaluated underthe conditions that the batteries were charged at 1.1 A for 1.5 hoursand a discharge cycle for discharging at 1 A was repeated until abattery voltage was 0.8 V. A cycle life was determined by the number ofcycles when the battery capacity was reduced to 50% of an initialcapacity.

Table 13 shows the result of the evaluation.

                  TABLE 13                                                        ______________________________________                                                                 Charge/Discharge                                     Battery No. Alloy Composition                                                                          Cycle (cycles)                                       ______________________________________                                        1           AB.sub.5.0   250                                                  2           .sub. AB.sub.5.05                                                                          360                                                  3           AB.sub.5.5   520                                                  4           AB.sub.5.8   490                                                  5           AB.sub.6.0   450                                                  6           AB.sub.6.2   120                                                  ______________________________________                                    

From Table 13, it is found that when non-stoichiometric composition isachieved, the cycle life is extended and when x of AB_(x) exceeds 6, thecycle life is rapidly shortened. It is found from the result of theX-ray diffraction analysis effected to the AB₆.2 alloy that the secondphase is grown in an amount of 10 vol % more, and from the result of theobservation by EPMA that a large amount of La and Mn is segregated tothe particle boundaries thereof, from which it is clear that thecreation of the second phase and the segregations to the particleboundaries greatly shorten the alloy life.

Comparative Example 24

A hydrogen-absorbing alloy having the same composition as that of theembodiment 20 was made by a conventional casting method. Materialsweighed so that the same composition as that of the embodiment 20 wasachieved were put into a crucible and melted in a high frequencyinduction heating furnace and then poured into a casting mode made ofiron to make the alloy. The thus obtained alloy was made tohydrogen-absorbing alloy electrodes in the same way as the embodiment 20and subjected to a powder X-ray diffraction analysis to observe thecreation of a second phase.

Table 14 shows the result of the analysis, wherein ∘ shows the creationof the single phase, x shows the creation of the second phase and Δshows the possibility of the creation the second phase in an amount of10 wt % or more, although not clear.

                  TABLE 14                                                        ______________________________________                                        Alloy Composition                                                                            Result of Analysis                                             ______________________________________                                        AB.sub.5.0     ∘                                                  .sub. AB.sub.5.05                                                                            Δ                                                        AB.sub.5.5     x                                                              AB.sub.5.8     x                                                              AB.sub.6.0     x                                                              AB.sub.6.2     x                                                              ______________________________________                                    

As apparent from Table 14, it is found that since a quenching rate isslow in the casting method, when the alloy is composed of thenon-stoichiometric composition, the second phase is liable to becreated. Although this may be improved by the use of a water-cooledcasting mold or reducing a casting thickness, it is very difficult tostably form the single phase up to the vicinity of the AB₅.5 where aperformance is greatly improved.

From the above mentioned facts, it is supposed that thehydrogen-absorbing alloy made by the molten-metal-rapidly-quenchingmethod is suitable as described in the embodiment 20.

Although the single roll method is described in the embodiment 20 as amethod of easily and stably making the hydrogen-absorbing alloy havingthe stoichiometric composition, the rotating disk method described inFIG. 32, double roll method described in FIG. 2, gas atomizing methoddescribed in FIG. 33 and other rotating nozzle method and the like asother molten-metal-rapidly-quenching methods also can stably provide thehydrogen-absorbing alloy having the stoichiometric composition in thesame way.

Although the embodiment 20 uses Ni, Co, Mn and Al as the elementsconstituting B of the hydrogen-absorbing alloy represented by AB_(x),the same result can be obtained by using, for example, Si, Fe, Cr, Cuand the like.

Embodiment 21

A hydrogen-absorbing alloy in an amount of 500 g having the compositionof Lm Ni₄.0 Co₀.4 Mn₀.3 Al₀.3 (Lm: La-rich misch metal) was melted in ahigh frequency induction furnace and accommodated to the ladle 2 of theaforesaid manufacturing apparatus employing the single roll method shownin FIG. 1 and a molten hydrogen-absorbing alloy 4 was dropped onto aroll (a cooling roll) 5 from the ladle 2 so that a flake-shapedhydrogen-absorbing alloy 6 was made. The alloy 6 was pulverized in aball mill and then classified through a 200 mesh sieve to makehydrogen-absorbing alloy powders for making electrode. Next, thehydrogen-absorbing alloy powders, PTFE powder and ketchen black wereweighed to 95.5 wt %, 4 wt % and 0.5 wt %, respectively and then stirredand mixed by a cutter mill until the PTFE was made to fibers. The thusobtained cotton-like mixture was scattered onto a nickel metal net androlled by a roller press to make hydrogen-absorbing alloy electrodes(negative electrodes).

Further, a paste separately prepared by adding a small amount of CMC and50 wt % of water to 90 wt % of nickel hydroxide and 10 wt % of cobaltmonoxide and stirring and mixing them. That paste was filled to a nickelporous member having a three-dimensional structure and dried and rolledby a roller press to make nickel electrodes (positive electrodes).

The hydrogen-absorbing alloy electrodes and nickel electrodes made bythe aforesaid method were used to assemble 30 kinds of AA type secondarynickel-metal hydride batteries which had the above negativeelectrode/positive electrode ratio and the amount of a batteryelectrolyte to the hydrogen-absorbing alloy electrodes shown in Table15. The capacity of these secondary batteries was set to 650 mAh as thetheoretical capacity of the nickel electrode and the battery electrolytewas composed of a solution mixed with 7N potassium hydroxide and 1Nlithium hydroxide. Further, a safety valve operating at 18 Kg/cm² wasused. Note, the portion in Table 15 in which battery symbols are notshown indicates that since an electrode volume is so large that apredetermined amount of the battery electrolyte cannot be poured intothe battery cans.

                  TABLE 15                                                        ______________________________________                                                     Negative Electrode/                                                           Positive Electrode Ratio                                                      0.5  1.1    1.5    2.0  2.5  3.0                                 ______________________________________                                        Amount of Battery                                                                         0.2    A1     A2   A3   A4   A5   A6                              Electrolyte to                                                                            0.4    B1     B2   B3   B4   B5   B6                              Hydrogen-absorbing                                                                        0.8    C1     C2   C3   C4   C5   C6                              Alloy Electrode                                                                           1.5    D1     D2   D3   D4   D5   --                              (ml/Ah)     1.8    E1     E2   E3   E4   --   --                                          2.0    F1     F2   F3   --   --   --                              ______________________________________                                    

The number of cycles of each of the respective secondary batteries,which belonged to the group of the symbol A (A1, A2, A3, A4, A5, A6),symbol group B (B1, B2, B3, B4, B5, B6), group of the symbol C (C1, C2,C3, C4, C5, C6), group of the symbol D (D1, D2, D3, D4, D5), group ofthe symbol E (E1, E2, E3, E4) and group of the symbol F (F1, F2, F3),was investigated until the capacity of the batteries was reduced to 50%of an initial capacity under the conditions that the batteries werecharged at 650 mA for 1.5 hours and then a discharge cycle dischargingat 1 A was repeated until the voltage of the batteries was 0.8 V. FIG.34 shows the result of the investigation. In FIG. 34, □ shows thecharacteristics of the group A batteries in Table 15, + shows thecharacteristics of the group B batteries in Table 15, ⋄ shows thecharacteristics of the group C batteries in Table 15, Δ shows thecharacteristics of the group D batteries in Table 15, x shows thecharacteristics of the group E batteries in Table 15, and ∇ shows thecharacteristics of the group F batteries in Table 15, respectively.

As apparent from FIG. 34, it is found that the secondary batterieshaving the negative electrode/positive electrode ratio of 0.5 have veryshort cycle life in all the amounts of the battery electrolyte. This isbecause that the arrangement of the batteries is limited by thehydrogen-absorbing alloy electrode and thus a capacity is only 0.5 timethe positive electrode and the internal pressure of the batteries isabruptly increased at an initial charge-discharge cycle to the pressureat which the safety valve is operated and the shortage of the batteryelectrolyte is caused because the electrolyte is discharged through thesafety valve. This fact is confirmed by the measurement of the internalpressure of the batteries and the check of disassembled batteriesexecuted separately.

On the other hand, the secondary batteries having the negativeelectrode/positive electrode ratio of 1.1 or higher achieve the cyclelife of 150 times or more under the charge/discharge conditions unlessthe amount of the battery electrolyte is excessively large orexcessively small. This cycle life is a value satisfying the cycle lifeof 500 cycles which can be practically employed in a secondary batteryin usual charge/discharge conditions and is supposed to be a sufficientcycle life. Even if the negative electrode/positive electrode ratio is1.1 or higher, however, when the amount of the battery electrolyte is0.2 ml/Ah to 2.0 ml/Ah, the cycle life is about 50 cycles which are notsatisfactory. This is because that the amount of the battery electrolyteis insufficient at an initial charge/discharge cycle under the conditionof 0.2 ml/Ah and the internal pressure of the batteries is increased tothe pressure valve operating pressure at the end of the charging underthe condition of 2.0 ml/Ah and thus the battery electrolyte wasgradually shorted. This fact is confirmed by the measurement of theinternal pressure of the batteries executed separately.

Further, the secondary batteries belonging to the groups A-F in Table 15were charged under the severe conditions of 650 mA for 5 hours and theinternal pressure thereof was measured to investigate the internalpressure characteristics of the batteries which had a large effect onthe battery life. FIG. 35 shows the result of the investigation. Note,in FIG. 35, □ shows the characteristics of the batteries of the group Ain Table 15, + shows the characteristics of the batteries of the group Bin Table 15, ⋄ shows the characteristics of the batteries of the group Cin Table 15, Δ shows the characteristics of the batteries of the group Din Table 15, x shows the characteristics of the batteries of the group Ein Table 15, and ∇ shows the characteristics of the batteries of thegroup F in Table 15, respectively.

It is found from FIG. 35 that the battery internal pressure of all ofthe secondary batteries having the negative electrode/positive electroderatio of 0.5 and secondary batteries having the amount of the batteryelectrolyte of 2 ml/Ah reaches 18 Kg/cm² at which the safety valve isoperated.

When the weights of these secondary batteries were measured before andafter the test, a loss of weight supposed to be caused by the leakage ofthe battery electrolyte was observed in a maximum amount of 300 mg andin a minimum amount of 40 mg.

The reason why the internal pressure of all the secondary batterieshaving the amount of the battery electrolyte of 0.2 ml/Ah is low in thisexperiment is that since the batteries had the very small amount of thebattery electrolyte and the internal resistance in the batteries wasabruptly increased, the output range of a constant current power supplyused for charging was exceeded to prevent a sufficient charging. Fromthis fact, it is found that the secondary batteries having the amount ofthe battery electrolyte of 0.2 ml/Ah cannot be practically used.

It is found from the above experiment for measuring the battery life andbattery internal pressure that the negative electrode/positive electroderatio must be 1.1 or higher and the amount of the battery electrolytemust be within the range of 0.4-1.8 ml per 1 Ah of thehydrogen-absorbing alloy electrode.

Further, there is admitted a tendency that the battery internal pressureis increased from the vicinity of the point where the negativeelectrode/positive electrode ratio exceeds 2. This is supposed to becaused by that since all the secondary batteries have the uniformcapacity of 650 mAh, the volume occupied by the group of the electrodesis increased in the batteries having the large negativeelectrode/positive electrode ratio and thus the space in the batteriesis reduced, from which it found that the amount of the batteryelectrolyte and negative electrode/positive electrode ratio haveinterdependent values and they cannot be independently determined in thedesign of battery.

Next, groups of electrodes each having a maximum capacity capable ofbeing accommodated in an AA type battery can were made when a certainnegative electrode/positive electrode ratio was given, batteries wereassembled with battery electrolytes having various conditions and pouredinto them, and the capacity of each of the batteries was measured in theinitial sound state of the batteries in order to confirm a high capacityas a large feature of a secondary nickel-metal hydride battery. FIG. 36shows the result of the measurement. Note, in FIG. 36,□ shows thecharacteristics of the secondary battery in which the amount of thebattery electrolyte to the hydrogen-absorbing alloy electrode is 0.2ml/Ah, + shows the characteristics of the secondary battery in which theamount of the battery electrolyte is 0.4 ml/Ah, ⋄ shows thecharacteristics of the secondary battery in which the amount of thebattery electrolyte is 0.8 ml/Ah, Δ shows the characteristics of thesecondary battery in which the amount of the battery electrolyte is 1.5ml/Ah, x shows the characteristics of the secondary battery in which theamount of the battery electrolyte is 1.8 ml/Ah, and ∇ shows thecharacteristics of the secondary battery in which the amount of thebattery electrolyte is 0.2 ml/Ah, respectively.

It is found from FIG. 36 that since the battery capacity of the batteryhaving the negative electrode/positive electrode ratio of 0.5 isdetermined by the hydrogen-absorbing alloy electrode, the capacity islow.

Further, the amount of the battery electrolyte of 0.2 ml/Ah is notsufficient to cause a battery reaction, the battery capacity is alsolow. In the batteries except the aforesaid ones, as the negativeelectrode/positive electrode ratio is increased, the capacity of thenickel electrode capable of being assembled in the volume of the samegroup of electrodes is reduced, and thus the battery capacity is alsoreduced.

Then, it is found that when the negative electrode/positive electroderatio exceeds 2.0, only a capacity similar to or less than that of thecurrently used high capacity type nickel-cadmium battery is obtained.

Although a higher capacity can be achieved by increasing the activatingmaterial density in electrode even if the negative electrode/positiveelectrode ratio is 2.0 or higher, in this case not only the manufactureof the electrode is difficult but also an oxygen reducing rate isgreatly lowered at the end of charging as well as large currentdischarging characteristics are also greatly lowered and thus thebattery using the electrode cannot be practically used.

It is found from this experiment that the negative electrode/positiveelectrode ratio must be 2.0 or less to enable secondary nickel-metalhydride battery to exhibit the feature of high capacity withoutsacrificing the battery characteristics.

Although the embodiment 21 describes in detail the example of the AAtype battery arranged by the hydrogen-absorbing alloy electrode as theactivating material obtained from the hydrogen-absorbing alloy made byrapidly quenching a molten alloy by the single roll method, non-sinterednickel electrode and battery electrolyte composed of the mixture of 7Npotassium hydroxide and 1N lithium hydroxide, the present invention isnot limited to this method.

For example, the hydrogen-absorbing alloy obtained by the rotating discmethod described in FIG. 32, double roll method described in FIG. 2, gasatomizing method described in FIG. 33 and the like as themolten-metal-rapidly-quenching method exhibited the same characteristicsas those obtained by the single roll method of this embodiment 21.

Further, with respect to the method of making electrode, the feature ofthe present invention can be also exhibited by a so-called paste typeelectrode made by filling or coating a kneaded material ofhydrogen-absorbing alloy powder, kneading agent and water with or to acollector and then drying and rolling the same. The abovehydrogen-absorbing alloy powder may be a powder obtained by beingpulverized by the absorption/release of hydrogen in addition to thepowder made by mechanically pulverizing a hydrogen-absorbing alloy madeby the molten-metal-rapidly-quenching method. In particular, when thesingle roll method or double roll method is employed, a flake-shapedhydrogen-absorbing alloy can be obtained under wide manufacturingconditions. Since this flake-shaped alloy is generally thin and can bepulverized relatively easily, it is possible that the alloy ispulverized only from several hundreds of microns to a few millimetersprior to the manufacture of electrode and further pulverized in therolling process for making the electrode together with the electrode.

The specific surface area of the hydrogen-absorbing alloy can be reducedby this processing in the manufacture of the electrode, thehydrogen-absorbing alloy can be protected from surface oxidation andpollution in the manufacturing process of the alloy as well as even thepossibility of firing of the hydrogen-absorbing alloy in themanufacturing process can be reduced, and thus an operation can beexecuted in a safe environment.

The battery electrolyte may be, for example, a 8N potassium hydroxidesolution or a battery electrolyte mixed with a sodium hydroxide solutionwhen necessary.

Further, with respect to a battery size, the same effect can be obtainedeven in the battery size of, for example, 4/5A type or A type inaddition to the AA type.

As described above in detail, according to this embodiment, there can beprovided a hydrogen-absorbing alloy which is less deteriorated when usedas a negative electrode activating material of a secondary alkalinebattery and has a long cycle life. Further, according to thisembodiment, a secondary nickel-metal hydride battery can be providedwhich has a high capacity and long life and can be made at a low cost byusing the a hydrogen-absorbing alloy electrode with a less amount ofdeterioration and limiting the amount of battery electrolyte andelectrode capacity ratio.

Next, the dispersion of Mn concentration in a hydrogen-absorbing alloyand the effect of the particle size of segregated Mn particles onbattery characteristics will be described below with reference to thefollowing embodiments and comparative examples.

Embodiments 22-23 and Comparative Embodiments 25-27

Lm, Ni, Co, Mn, Al were weighed, previously taking the amount of themlost when they were melted into consideration, so that these materialshad the composition of Lm Ni₄.3 Co₀.1 Mn₀.5 Al₀.1 (Lm: La-rich mischmetal) when made to an alloy.

Next, these materials were melted in a high frequency induction furnaceand flowed into a usual casting mold to provide the alloy for acomparative example 25 and flowed into a water-cooled casting mold toprovide the alloy for a comparative example 26 with a thickness of 10mm. Further, in the single roll method shown in FIG. 1, a copper rollwith a diameter of 300 mm was used as the cooling roll 5 and rotated at600 rpm in vacuum, the distance between the injection nozzle 4 and thecooling roll 5 was set to 50 mm and an injection pressure was set to 0.1Kgf/cm² so that the alloy with a thickness of about 100 microns for acomparative example 27 was provided. Further, the injection pressure wasset to 0.05 Kgf/cm² so that the alloy with a thickness of about 50microns for an embodiment 22 was provided. Further, the injectionpressure was set to 0.02 Kgf/cm² so that the alloy with a thickness ofabout 20 microns for an embodiment 23 was provided. Thus, three kinds ofthe specimens of the flake-shaped alloys were made. In addition to theabove, a hydrogen-absorbing alloy powder with an average particle sizeof 20 microns was prepared as an embodiment 24 by the inert gasatomizing method shown in FIG. 33.

The distribution of Mn concentration in these alloy specimens wasinvestigated by the following method.

1) Burying of Resin

An alloy specimen was taken in an amount of 100 mg and dispersed to thecenter of a resin burying frame (made of polypropylene) with a diameterof 20 mm for SEM specimen.

Next, an epoxy resin (EPO-MIX made by Buller Ltd.) commerciallyavailable as a resin for burying SEM specimen and a curing agent weresufficiently mixed and then the thus obtained mixed material was pouredinto the burying frame and cured. At that time, it was furtherpreferable to preheat the resin to about 60° C. to lower the viscositythereof or to remove foams therefrom by evacuating the resin in a vacuumdesiccator after it had been poured into the frame to improve theintimate contact property of the resin with the specimen.

2) Polishing

Next, the specimen buried by the above procedure was polished by arotary polishing machine until it was mirror-polished. Since thespecimen of the hydrogen-absorbing alloy was liable to react with water,it was polished with water-resistant abrasive papers mounted on thepolishing machine rotating at 200 rpm while dropping methyl alcohol. Atthat time, the abrasive papers were sequentially changed to finer onesof #180, #400 and #800. Then, the specimen was mirror-polished by thediamond paste on the rotary polishing machine having a felt set thereon,the felt being provided with the diamond paste whose grain size was madefiner in the sequence of 15 microns, 3 microns and 0.25 micron.

3) Observation by EPMA

Next, each of these specimens were set to an EPMA (Model V6, made byShimazu Seisakusho). First, a region where Mn is not contained at all(e.g., a specimen table) was observed to perform a mapping observationand the intensity value of characteristic X-rays was recorded when a Mnconcentration was 0. Next, the specimen was moved so that it was locatedat the center of a visual field and the entire image of the distributionof the Mn concentration was grasped by the mapping observation. Note, inthe measurement, a magnification was set such that an observation regionof 20×20 microns was within the visual field. Further, at that time, acaution was taken so that the edge of the specimens was not located inthe visual field. Then, the visual field was vertically and horizontallydivided into 100 portions to form 10000 pieces of unit regions and theEPMA was set to measure the intensity value of the X-rays for eachregion.

The distribution of the characteristic X-ray intensity within theobserved surface obtained by the above observation was corrected by thepreviously determined intensity value within the region in which Mn wasnot contained.

The average value of the characteristic X-ray intensity within theobserved surface was determined by simply averaging the characteristicX-ray intensity corresponding to the respective unit regions obtained asdescribed above. Further, the maximum value of the characteristic X-rayintensity was used as a maximum value. Further, the ratio of the maximumvalue to the average value of the X-ray intensity was calculated.

The above analysis was performed 10 times while changing the visualfield.

Table 16 shows the result of the analysis. Further, Table 16 also showsthe quenching rates when the specimens were made, the quenching rates(cooling speeds) being measured by the same method as that in theembodiments 18A-18C.

                  TABLE 16                                                        ______________________________________                                                  Max.     Average  Max. Intensity                                                                          Quenching                                         Intensity                                                                              Intensity                                                                              Value/Average                                                                           Rate                                    Specimen No.                                                                            Value    Value    Intensity Value                                                                         (°C./S)                          ______________________________________                                        Comparative                                                                             68       48       1.42      80                                      Example 25                                                                    Comparative                                                                             70       51       1.37      250                                     Example 26                                                                    Comparative                                                                             64       47       1.36      1000                                    Example 27                                                                    Embodiment 22                                                                           60       49       1.22      2000                                    Embodiment 23                                                                           60       52       1.15      3000                                    Embodiment 24                                                                           60       50       1.20      50000                                   ______________________________________                                    

It is found from Table 16 that the ratio of the maximum intensity valueto the average intensity value is lowered in the sequence of thecomparative example 25, comparative example 26, comparative example 27,embodiment 22, embodiment 24, and embodiment 23.

Next, Table 17 shows the result of observation of the crystal types ofthe respective specimens observed by the method described in theembodiments 1-9.

                  TABLE 17                                                        ______________________________________                                        Area Ratio of Columnar Structures (%)                                                                     Minor                                             Aspect Ratio                    Dia of                                                1:2     1:3     1:4   1:5         Columnar                            Specimen                                                                              or      or      or    or    As a  Structures                          No.     higher  higher  higher                                                                              higher                                                                              Whole (μm)                             ______________________________________                                        Comparative                                                                           Max. Crystal Grain Size 180 μm                                     Example 25                                                                    Comparative                                                                           19      10       3     2     9    9.5                                 Example 26                                                                    Comparative                                                                           39      28      21    10    11    1.9                                 Example 27                                                                    Embodiment                                                                            71      69      62    51    33    2.7                                 22                                                                            Embodiment                                                                            95      89      82    89    69    2.5                                 23                                                                            Embodiment                                                                            Max. Crystal Grain Size 10 μm                                      24                                                                            ______________________________________                                    

In Table 17, the reason why no numerical value is shown in thecomparative example 25 and embodiment 24 is that an equi-axed crystalstructure is observed on the entire cross section of the comparativeexample 25 and a columnar structure is not recognized therein, andfurther in the embodiment 24 a structure other than the columnarstructure is also formed, although the kind of the structure cannot berecognized.

When Table 16 is compared with Table 17, the reason why there is thecorrespondence between the ratio of columnar structures and theuniformity of the Mn distribution in the comparative examples 26, 27 andthe embodiments 22 and 23 is as described below. That is, when thequenching rate is high as in the case of the embodiments 22, 23, themolten alloy is rapidly quenched and solidified and the solidificationprogresses in one direction from the quenched surface and columnarstructures are liable to be grown so that the ratio of the columnarstructures is increased.

Further, it is supposed that since the molten alloy is rapidlysolidified, particular elements cannot exist in a molten state for theperiod of time necessary for the particular elements to formsegregations in particles and particle boundaries and thus even theelement such as Mn liable to produce an irregular distribution andsegregations is solidified while keeping the uniformity of distribution.

Further, it is supposed that the reason why the embodiment 24 isexcellent in the uniformity of Mn distribution regardless of that nocolumnar structure is recognized therein is that since the quenchingrate is also very high and particular elements cannot exist in a moltenstate for the time necessary for the elements to form segregations inparticles and particle boundaries, even the element such as Mn liable toproduce an irregular distribution and segregations is solidified whilekeeping the uniformity of distribution.

Next, electrodes were made by using these specimens by using thefollowing procedure. First, the above alloys were pulverized in a ballmill and the particles thereof larger than 200 mesh were removed by a200 mesh sieve to provide hydrogen-absorbing alloy powders. Next, thehydrogen-absorbing alloy powders, PTFE powder and ketchen black wereweighed to 95.5 wt %, 4 wt % and 0.5 wt %, respectively and then stirredand mixed by a cutter mill until the PTFE was made to fibers. The thusobtained cotton-like mixture was dispersed onto a nickel metal net androlled by a roller press to make hydrogen-absorbing alloy electrodes.

Each of these electrodes was bound with a sintered type nickel electrodethrough a nylon separator and immersed into a 8N potassium hydroxidesolution and the cycle life thereof was evaluated throughcharging/discharging.

The evaluation was carried out by repeating a charge/discharge cycleunder the conditions that charging was effected for 1 hour at a currentof 220 mA per 1 g of the alloy in the electrode and discharging waseffected also at the current of 220 mA until -0.5 V was achieved to aHg/HgO electrode. A cycle life was determined by the number of cycleswhen an electrode capacity was lowered to 50% of an initial electrodecapacity. The evaluation was performed at 20° C. FIG. 37 shows thechange of capacity as the cycle proceeds and Table 18 shows the cyclelife.

                  TABLE 18                                                        ______________________________________                                                        Max. Intensity Value/                                                                        Cycle Life                                     Specimen No.    Average Intensity Value                                                                      (cycles)                                       ______________________________________                                        Comparative Example 25                                                                        1.42           320                                            Comparative Example 26                                                                        1.37           350                                            Comparative Example 27                                                                        1.36           400                                            Embodiment 22   1.22           700                                            Embodiment 23   1.15           740                                            Embodiment 24   1.20           620                                            ______________________________________                                    

As shown in the above, it is confirmed that in the comparative examples25-27 in which the X-ray intensity ratio to the Mn concentration in thehydrogen-absorbing alloy is about 1.2, the cycle life of the electrodeis about 350 cycles, whereas in the embodiments 22-24 in which an X-rayintensity ratio is 1.3 or less which is within the range of the presentinvention, the cycle life in the electrode is greatly extended to620-740 cycles.

Next, to investigate the performance in actual batteries, batteries wasmade in the following procedure by using these alloys and the cycle lifethereof was evaluated.

The hydrogen-absorbing alloy electrodes were made by the same method asthat of the above electrodes for evaluation.

Note, a caution was taken so that the amount of the hydrogen-absorbingalloy in the electrodes was set to 9 g±0.2 g.

A nickel electrode was made in such a manner that a paste was preparedby adding a small amount of CMC and 50 wt % of water to 90 wt % ofnickel hydroxide and 10 wt % of cobalt monoxide and stirring and mixingthem and filled with a nickel porous member having a three-dimensionalstructure and dried and rolled by a roller press. At that time, acapacity calculated from the weight of the nickel hydroxide in theelectrode was set to 1.1 Ah.

Each of the thus made hydrogen-absorbing alloy electrodes and the nickelelectrode were combined and wound separated by a polypropylene non-wovenfabric to provide groups of electrodes. Each of the groups of theelectrodes was inserted into a battery can, and the can was filled witha solution mixed with 7N potassium hydroxide and 1N lithium hydroxide asan battery electrolyte and sealed by the terminal plate of a positiveelectrode having a safety valve operating at a pressure of 15 Kg/cm² toassemble a test battery shown in FIG. 3.

The cycle life was evaluated by using these batteries by repeating acharge/discharge cycle under the conditions that each battery wascharged at 1.1 A for 1.5 hours and then discharged at 1 A until abattery voltage was 0.8 V. A cycle life was determined by the number ofcycles when the battery capacity was lowered to 50% of an initialcapacity. A test temperature was 25° C. FIG. 38 shows the change ofcapacity as the cycle proceeds and Table 19 shows the cycle life.

Note, at this time, it is confirmed that the uniformity of Mndistribution can be also observed in the electrodes made to battery bythe following procedure in the same way as the case of the alloy.

1) Discharge of Battery

First, batteries in which a charge/discharge cycles were not progressedafter they had been made were prepared as specimens. As acharge/discharge cycle progressed, the Mn uniformity in an alloy waschanged and thus it was preferable that the number of thecharge/discharge cycle of the batteries used as the specimens was 10cycles or less, if possible.

These batteries were discharged in a battery state at a current of 110mA until a voltage was 0.8 V and then remained they were for 10 hourswith a resistance of 10KΩ connected between the electrodes of each ofthe batteries so that they were perfectly discharged. The reason why thebatteries were discharged in the two steps was to prevent firing causedby remaining hydrogen.

2) Washing of Electrode

After the completion of the discharge, the batteries were disassembledand the hydrogen-absorbing alloy electrodes were taken out therefrom.The thus taken-out alloy electrodes were sufficiently washed with purewater and then perfectly dried in a vacuum drier for the purpose ofremoving hydrogen remaining in the electrodes and preventing theinsufficient solidification of the resin caused by the batteryelectrolyte and the strength by which the specimens were attached to theresins from being lowered.

3) Burying of Resin

Each of the dried electrodes was cut off to the size of about 10 mm×5 mmand dispersed to the center of a resin burying frame (made ofpolypropylene) with a diameter of 20 mm for SEM specimen. Next, an epoxyresin (EPO-MIX made by Buller Ltd.) commercially available as a resinfor burying a SEM specimen and a curing agent were sufficiently mixedand then the thus obtained mixed material was poured into the buryingframe and cured. At that timer it was further preferable to preheat theresin to about 60° C. to lower the viscosity thereof or to remove foamstherefrom by evacuating the resin in a vacuum desiccator after it hadbeen poured into the frame to improve the intimate contact property ofthe resin with the specimen.

4) Polishing

Next, the specimen buried by the above procedure was polished by arotary polishing machine until it was mirror-polished. Since thespecimen of the hydrogen-absorbing alloy was liable to react with water,it was polished with water-resistant abrasive papers mounted on thepolishing machine rotating at 200 rpm while dropping methyl alcohol. Atthat time, the abrasive papers were sequentially changed to finer onesof #180, #400 and #800. Then, the specimen was mirror-polished by thediamond paste on the rotary polishing machine having a felt set thereon,the felt being provided with the diamond paste whose grain size was madefiner in the sequence of 15 microns, 3 microns and 0.25 micron.

5) Observation by EPMA

Next, the average value and maximum value of the X-ray intensitycorresponding to the Mn concentration in the specimens were measured inthe same procedure as above by using an EPMA.

Table 20 shows the result of the measurement, wherein substantially thesame numerical values as those in Table 16 are obtained and thus it isconfirmed that observation is sufficiently possible even after thealloys have been made to electrode and battery.

                  TABLE 19                                                        ______________________________________                                                          Cycle Life                                                  Specimen No.      (cycles)                                                    ______________________________________                                        Comparative Example 25                                                                          95                                                          Comparative Example 26                                                                          130                                                         Comparative Example 27                                                                          170                                                         Embodiment 22     480                                                         Embodiment 23     510                                                         Embodiment 24     410                                                         ______________________________________                                    

                  TABLE 20                                                        ______________________________________                                                  Max. Intensity                                                                           Average  Max. Intensity Value/                           Specimen No.                                                                            Value      Intensity                                                                              Average Intensity Value                         ______________________________________                                        Comparative                                                                             69         48       1.44                                            Example 25                                                                    Comparative                                                                             68         50       1.36                                            Example 26                                                                    Comparative                                                                             67         50       1.34                                            Example 27                                                                    Embodiment 22                                                                           57         47       1.21                                            Embodiment 23                                                                           59         50       1.18                                            Embodiment 24                                                                           60         50       1.20                                            ______________________________________                                    

As shown in the above, in the batteries using the alloys of thecomparative examples 25-27 having the low uniformity of the Mndistribution, the increase of the internal pressure of the batteriescaused by the deterioration of the hydrogen-absorbing alloys is admittedfrom the relatively initial stage of the charge/discharge cycles, in thesame way as the result of the above evaluation of electrodes. Since thebattery electrolyte is flown out from the safety valve by the increaseof the internal pressure, battery capacities are reduced and thus thecycle life of only about 130 cycles is obtained. Whereas, the internalpressure of the batteries using the alloys of the embodiments 22-24having improved uniformity is relatively gradually increased, and as aresult the cycle life of 410 to 510 cycles is successfully obtained inthe batteries which greatly exceeds 300 cycles as the practical life ofa secondary battery. Thus, it is confirmed that the cycle life can begreatly increased even in actual batteries by setting the uniformity ofthe Mn distribution within the range of the present invention.

Embodiments 25, 26 and Comparative Examples 28, 29

Lm, Ni, Co, Mn, Al were weighed, previously taking the amount of themlost when they were melted into consideration, so that these materialshad the composition of Lm Ni₄.0 Co₀.4 Mn₀.3 Al₀.3 (Lm: La-rich mischmetal) when made to an alloy.

Next, these materials were melted in a high frequency induction furnaceand flowed into a usual casting mold to make the alloy for a comparativeexample 28. Further, in the single roll method shown in FIG. 1, a copperroll with a diameter of 300 mm was used as the cooling roll and rotatedat 800 rpm in vacuum, the distance between the injection nozzle and thecooling roll was set to 50 mm and an injection pressure was set to 0.1Kgf/cm² so that the alloy with a thickness of about 100 microns wasprepared for a comparative example 29. Further, the injection pressurewas set to 0.02 Kgf/cm² so that a flake-shaped alloy specimen with athickness of 20 microns was made for an embodiment 25. In addition tothe above, a hydrogen-absorbing alloy powder with an average particlesize of 20 microns was prepared as an embodiment 26 by the inert gasatomizing method shown in FIG. 33.

The size of the segregated Mn in these alloy specimens was investigatedby the method described below. First, the alloy specimens were sealed insynthetic resin by the same procedure as the embodiments 22-24 andmirror-polished by a polisher.

Next, each of the specimens was set to SEM (Model ABT-55 made by ABT)with EDX (made by KEVEX) and observed. First, a mapping observation ofthe Mn and other elements constituting the hydrogen-absorbing alloy wasperformed by the EDX and the locations where Mn was independentlysegregated were searched. Since, however, the EDX had a lower resolutionas compared with that of the EPMA and it was difficult to directlydetermine the size of the segregations from the result of the mappingobservation, the points having high Mn concentration determined by theEDX had to be observed by the SEM to correctly find the size of thesegregations of Mn. That is, since the points where the concentration ofMn and other elements was different from the alloy composition wereobserved as the points where the intensity of a reflected electron beamwas different from that of the alloy portion in the SEM, the reason whythe intensity was different was determined by the EDX and then the sizeof a region was determined from the result of observation by the SEM.

Table 21 shows the result of observation of the size of segregations ofMn of the comparative examples 28,29 and embodiments 25 and 26 performedby the SEM and EDX. Note, 10 visual fields were observed for eachspecimen to prepare Table 21.

                  TABLE 21                                                        ______________________________________                                                         Max. Diameter of                                                              Segregated Mn                                                Specimen No.     (μm)                                                      ______________________________________                                        Comparative Example 28                                                                         1.52                                                         Comparative Example 29                                                                         0.71                                                         Embodiment 25    0.41                                                         Embodiment 26    0.10                                                         ______________________________________                                    

Next, the crystal types of the respective specimens were observed by themethod described in the embodiments 1-9 and Table 22 shows the result ofthe observation.

                  TABLE 22                                                        ______________________________________                                        Area Ratio of Columnar Structures (%)                                                                     Minor                                             Aspect Ratio                    Dia of                                                1:2     1:3     1:4   1:5         Columnar                            Specimen                                                                              or      or      or    or    As a  Structures                          No.     higher  higher  higher                                                                              higher                                                                              Whole (μm)                             ______________________________________                                        Comparative                                                                           Max. Crystal Grain Size 160 μm                                     Example 28                                                                    Comparative                                                                           17      11       3     1    10    9.0                                 Example 29                                                                    Embodiment                                                                            88      72      62    51    89    2.7                                 25                                                                            Embodiment                                                                            Max. Crystal Grain Size 10 μm                                      26                                                                            ______________________________________                                    

In Table 22, the reason why no numerical value is shown in thecomparative example 28 and embodiment 26 is that an equi-axed crystalstructure is observed on the entire surface of the comparative example28 and a columnar structure is not recognized therein, and further inthe embodiment 26 a structure other than the columnar structure is alsoformed, although the kind of the structure cannot be clearly recognized.

When Table 21 is compared with Table 21, the reason why there is acorrespondence between the ratio of columnar structures and the size ofMn segregations in the comparative examples 29 and embodiments 25 is asdescribed below. That is, when a quenching rate is high as in the caseof the comparative example 29 and embodiments 25, the molten alloy israpidly quenched and solidified, and the solidification is liable toprogress in a given direction from the quenched surface and thuscolumnar structures are liable to be grown so that the ratio of thecolumnar structures is increased. Further, it is supposed that since themolten alloy is rapidly solidified, particular elements cannot exist ina molten state until the time at which the particular elements formsegregations in the particles and particle boundaries, and even if thesegregations are made, they are difficult to be grown, and thus even theelement such as Mn liable to be segregated cannot be made to a largesegregated material. Further, the reason why in the embodiment 26 the Mnsegregations have a small size regardless of that no columnar structureis admitted is supposed to be that since a quenching rate is also veryhigh, particular elements cannot exist in a molten state until the timeat which the particular elements form segregations in the particles andparticle boundaries, and even if the segregations are made, they aredifficult to be grown, and thus even the element such as Mn liable to besegregated cannot be made to a large segregated material.

Next, these specimens each in an amount of 20 g were sealed in a sealedvessel (volume: 50 cc) with a gas introduction pipe and the sealedvessel absorbed hydrogen pressurized to 10 Kg/cm² through the pipe whilethe vessel was immersed into cooled water of 10° C. and then thehydrogen was released from the sealed vessel by connecting the pipe to avacuum pump while the vessel was immersed in hot water of 60° C. Afterthe repetition of the absorption and release of the hydrogen 1000 times,the distribution of particles of the specimens were measured by a laserscattering type particle distribution measuring instrument (made bySeishin Kigyo Co.) Table 23 shows the result of the measurement.

                  TABLE 23                                                        ______________________________________                                                         Particle Size of                                                              Hydrogen-absorbing                                           Specimen No.     Alloy (μm)                                                ______________________________________                                        Comparative Example 28                                                                         9                                                            Comparative Example 29                                                                         13                                                           Embodiment 25    27                                                           Embodiment 26    17                                                           ______________________________________                                    

It is found from Table 23 that in the embodiment 25 having the Mnsegregations whose size is small and within the range of the presentinvention, even if the absorption/release of hydrogen is repeated 1000times, the average size of 35 microns prior to the test is reduced onlyto 27 microns and the average size of 20 microns in the embodiment 26 isreduced only to 17 microns, and thus it is found that the pulverizationcaused by the absorption/release of hydrogen to the hydrogen-absorbingalloy is restricted. On the other hand, it is confirmed that the initialaverage size of 35 microns in the comparative examples 28 and 29 isreduced to 9 microns and 13 microns, respectively.

Next, a cycle life test was executed to electrodes to confirm the effectof the difference in the pulverizing behavior confirmed in the abovetest on the actual electrode characteristics.

Here, electrodes were made by the following procedures. First, the abovealloys were pulverized in a ball mill and the particles thereof largerthan 200 mesh were removed by a 200 mesh sieve to providehydrogen-absorbing alloy powders.

Next, the hydrogen-absorbing alloy powders, PTFE powder and ketchenblack were weighed to 95.5 wt %, 4 wt % and 0.5 wt %, respectively andthen stirred and mixed by a cutter mill until the PTFE was made tofibers. The thus obtained cotton-like mixture was scattered onto anickel metal net and rolled by a roller press to make hydrogen-absorbingalloy electrodes.

Each of the electrodes was bound to a sintered type nickel electrodethrough a nylon separator and immersed into a 8N potassium hydroxidesolution and the cycle life thereof was evaluated through charging anddischarging.

The evaluation was carried out by repeating a charge/discharge cycleunder the conditions that charging was effected for 1 hour at a currentof 220 mA per 1 g of the alloy in the electrode and discharging waseffected also at the current of 220 mA per 1 g of the alloy until -0.5 Vwas achieved to a Hg/HgO electrode. The number of cycles was determinedby the cycle life when an electrode capacity was lowered to 50% of aninitial electrode capacity. The evaluation was performed at 20° C. Table24 shows the cycle life.

                  TABLE 24                                                        ______________________________________                                                          Cycle Life                                                  Specimen No.      (cycles)                                                    ______________________________________                                        Comparative Example 28                                                                          330                                                         Comparative Example 29                                                                          380                                                         Embodiment 25     725                                                         Embodiment 26     650                                                         ______________________________________                                    

When the result of Table 24 is compared with that of Table 23, it isfound that the comparative examples 28, 29 in which pulverization isliable to be progressed has a shorter life than the embodiments 25, 26in which pulverization is restricted and it is confirmed that the cyclelife can be remarkably extended by the restriction of the progress ofpulverization.

Note, at this time, it is confirmed that the size of Mn segregations inthe alloy made to electrode by the following procedures also can beobserved in the same way as alloy as a single body.

1) Discharge of Electrode

First, electrodes in which a charge/discharge cycles were not progressedafter they had been made were prepared as specimens. As thecharge/discharge cycle progressed, the state of Mn segregations in thealloys was changed and thus it was preferable that the number of thecharge/discharge cycle of the electrodes used as the specimens was 10cycles or less, if possible. These electrodes were discharged at acurrent of 0.1 A until -0.5 V was achieved to a Hg/HgO electrode so thatthey were perfectly discharged. The reason why the they were perfectlydischarged was to prevent firing caused by remaining hydrogen.

2) Washing of Electrode

After the completion of the discharge, the hydrogen-absorbing alloyelectrodes were sufficiently washed with pure water and then perfectlydried in a vacuum drier for the purpose of removing hydrogen remainingin the electrodes and preventing the insufficient solidification ofresins caused by the battery electrolyte and the strength by which thespecimens were attached to the resins from being lowered.

3) Burying of Resin

Each of the dried electrodes was cut off to the size of about 10 mm×5 mmand dispersed to the center of a SEM resin burying frame (made ofpolypropylene) with a diameter of 20 mm for SEM specimen. Next, an epoxyresin (EPO-MIX made by Buller Ltd.) commercially available as a resinfor burying a SEM specimen and a curing agent were sufficiently mixedand then the thus obtained mixed material was poured into the buryingframe and cured. At that time, it was further preferable to preheat theresin to about 60° C. to lower the viscosity thereof or to remove foamstherefrom by evacuating the resin in a vacuum desiccator after it hadbeen poured into the frame to improve the intimate contact property ofthe resin with the specimen.

4) Polishing

Next, the specimen buried by the above procedure was polished by arotary polishing machine until it was mirror-polished. Since thespecimen of the hydrogen-absorbing alloy was liable to react with water,it was polished with water resistant abrasive papers mounted on thepolishing machine rotating at 200 rpm while dropping methyl alcohol. Atthis time, the abrasive papers were sequentially changed to finer onesof #180, #400 and #800. Then, the specimen was mirror-polished by thediamond paste on the rotary polishing machine on which a felt was setwith the grain size of the diamond paste made finer in the sequence of15 microns, 3 microns and 0.25 micron.

5) Observation by EDX

Next, each of the specimens was set to SEM (Model ABT-55 made by ABT)with EDX (made by KEVEX) and observed. First, a mapping observation ofthe Mn and other elements constituting the hydrogen-absorbing alloy wasperformed by the EDX and the locations where Mn was independentlysegregated were searched. Since, however, the EDX had a lower resolutionas compared with that of the EPMA and it was difficult to directlydetermine the size of the segregations from the result of the mappingobservation, the points with high Mn concentration determined by the EDXhad to be observed by the SEM to correctly find the size of thesegregations of Mn. That is, since the points where the concentration ofMn and other elements was different from the alloy composition wereobserved as the points where the intensity of a reflected electron beamwas different from that of the alloy portion in the SEM, the reason whythe intensity was different was determined by the EDX and then the sizeof a region was determined from the result of observation by the SEM.

The above analysis was performed 10 times while changing the visualfield.

Although Ni, Co, Mn, Al were used as the elements constituting B in theabove embodiment, the same effect could be obtained even if a partthereof was substituted for Cr, Si, Fe, Cu, Ag, Pd, Sn, In, Ga, Ge, Ti,Zr, Zn or the like.

As described above in detail, the corrosion resistance of the alloysagainst a thick alkaline solution as a battery electrolyte is improvedas well as the pulverization caused by the expansion/shrinkage due tothe absorption/release of hydrogen can be suppressed by setting themaximum value of Mn concentration in the hydrogen-absorbing alloyscontaining Mn which is very effective to increase the capacity of thehydrogen-absorbing alloys to 1.3 times or less the average value thereofor setting the maximum diameter of Mn segregated in the alloys to 0.1micron or less, whereby the life of the hydrogen-absorbing alloys can beextended. As a result, the life of the secondary nickel-metal hydridebattery employing these alloys can be extended. Consequently, thehydrogen-absorbing alloys according to the present invention have a verylarge industrial value.

As described above, since the first to third hydrogen-absorbing alloysfor battery of the present invention are composed of an AB₅ type alloycontaining Mn as an essential element, the hydrogen-absorbing alloys canprovide a negative electrode material having a high capacity andexcellent cycle life and initial characteristics when used to secondaryalkaline battery.

Further, when the alloys are subjected to a heat treatment at arelatively low temperature of about 200°-500° C., the internaldistortion of the alloys can be removed while keeping the homogeneitythereof, and thus the alloys can provide nickel-metal hydride batteryhaving more excellent battery characteristics.

Further, the method of manufacturing hydrogen-absorbing alloys accordingto the present invention can provide a negative electrode materialhaving a high capacity and excellent cycle life and initialcharacteristics for secondary nickel-metal hydride battery.

Further, the fourth hydrogen-absorbing alloy according to the presentinvention can form electrode having a less amount of deterioration andlong cycle life when used as a negative electrode activating material.

Further, the secondary nickel-metal hydride battery according to thepresent invention has a high capacity and long life and can be made atlow cost.

What claimed is:
 1. A method of manufacturing a hydrogen-absorbing alloyfor a battery, comprising the step of:injecting a molten alloy havingthe composition represented by a general formula A Ni_(a) Mn_(b) M_(c)where A is at least one element selected from the group consisting ofrare earth elements including Y (yttrium), M is a metal mainly composedof at least one element selected from the group consisting of Co, Al,Fe, Si, Cr, Cu, Ti, Zr, Zn, Hf, V, Nb, Ta, Mo, W, Ag, Pd, B, Ga, In, Geand Sn, 3.5≦a≦5, 0.1≦b≦1, 0≦c≦1, 4.5≦a+b+c≦6 onto the traveling surfaceof a cooling roll(s) rotating at a high speed; and rapidly quenching andsolidifying said molten alloy at a quenching rate of 1800° C./sec. orhigher to prepare a rapidly-quenched molten alloy to provide saidhydrogen-absorbing alloy for a battery, wherein said hydrogen-absorbingalloy has columnar structures in which an area ratio of the columnarstructures having the ratio of a width to a length (aspect ratio) of 1:2or higher is 50% or more, and said columnar structures have an averagewidth of 30 microns or less.
 2. A method of manufacturing ahydrogen-absorbing alloy for a battery according to claim 1, whereinsaid molten alloy is rapidly quenched in vacuum.
 3. A method ofmanufacturing a hydrogen-absorbing alloy for a battery, comprising thesteps of:rapidly quenching a molten alloy having the compositionrepresented by a general formula A Ni_(a) Mn_(b) M_(c) where A is atleast one element selected from the group consisting of rare earthelements including Y (yttrium), M is a metal mainly composed of at leastone element selected from the group consisting of Co, Al, Fe, Si, Cr,Cu, Ti, Zr, Zn, Hf, V, Nb, Ta, Mo, W, Ag, Pd, B, Ga, In, Ge and Sn,3.5≦a≦5, 0.1≦b≦1, 0≦c≦1, 4.5≦a+b+c≦6 to prepare a rapidly-quenchedmolten alloy; and subjecting said obtained rapidly-quenched molten alloyto a heat treatment at a temperature range of 200°-500° C. for at leastone hour for forming a hydrogen-absorbing alloy for a battery, whereinsaid hydrogen-absorbing alloy has columnar structures in which an arearatio of the columnar structures having the ratio of a width to a length(aspect ratio) of 1:2 or higher is 50% or more, and said columnarstructures have an average width of 30 microns or less.
 4. A method ofmanufacturing a hydrogen-absorbing alloy for a battery according toclaim 3, wherein said rapidly quenched molten alloy is formed byinjecting a molten alloy onto the traveling surface of a cooling roll(s)rotating at a high speed and rapidly quenching the same and theperipheral speed of the traveling surface of said cooling roll(s) is setto the range of 5-15 m/sec.
 5. A method of manufacturing ahydrogen-absorbing alloy for a battery according to claim 3, whereinsaid molten alloy is rapidly quenched in vacuum.
 6. A method ofmanufacturing a hydrogen-absorbing alloy for a battery according toclaim 3, wherein said heat treatment is carried out in vacuum or aninert gas atmosphere.